Cover glass and method for producing cover glass

ABSTRACT

The disclosed cover glass is produced by etching a glass substrate that has been formed by a down-drawing process, and chemically strengthening the glass substrate to provide the glass substrate with a compressive-stress layer on the principal surfaces thereof. The glass substrate contains, as components thereof, 50% to 70% by mass of SiO 2 , 5% to 20% by mass of Al 2 O 3 , 6% to 30% by mass of Na 2 O, and 0% to less than 8% by mass of Li 2 O. The glass substrate may also contain 0% to 2.6% by mass of CaO, if necessary. The glass substrate has an etching characteristic in which the etching rate is at least 3.7 μm/minute in an etching environment having a temperature of 22° C. and containing hydrogen fluoride with a concentration of 10% by mass.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation of U.S. patent application Ser. No.13/247,627, filed on Sep. 28, 2011, which claims the benefit of priorityof Japanese Patent Application No. 2010-222826, filed on Sep. 30, 2010and Japanese Patent Application No. 2010-294557, filed on Dec. 29, 2010,the entire contents of U.S. patent application Ser. No. 13/247,627,Japanese Patent Application No. 2010-222826 and Japanese PatentApplication No. 2010-294557 are incorporated herein by reference.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a cover glass that is subjected toshape-processing by etching and that is chemically-strengthened so as tohave a compressive-stress layer on its principal surfaces, and to amethod for producing the cover glass. The cover glass produced accordingto an embodiment of the present disclosure can be employed, for example,as a glass plate used as a component for protecting the display screenor the like of equipment such as a mobile phone, a personal digitalassistant (PDA), a digital camera, or a flat panel display (FPD).

2. Background Art

Strengthened glasses produced by chemically strengthening glasssubstrates have been conventionally used, for example, as covermaterials for protecting the liquid-crystal display screens etc. ofequipment such as mobile phones, PDAs, digital cameras, and FPDs. Theglass substrates are strengthened by an ion-exchange process.

In recent years, mobile phones and PDAs have tended to become thinner,more sophisticated in functionality, and more complicated in shape.Thus, strengthened glasses used as cover glasses in equipment such asmobile phones and PDAs are required to have formed therein recessesand/or holes with negative curvatures. Herein, what is meant by anegative curvature is that, if a point that is located on and movesalong the contour of a given region keeps turning toward the right whilethe inner section of the region is always located on the left-hand sideof the point, then the contour of said region is considered as having anegative curvature. On the other hand, the contour is considered ashaving a positive curvature if the point keeps turning toward the leftas it moves along the contour while the inner section of the region isalways located on the left-hand side of the point. The contour isconsidered as having zero curvature if the point keeps moving straightforward. It is, however, difficult to subject a strengthened glass toouter-shape processing to form recesses or holes that include sectionswith negative curvatures, because the strengthened glass has acompressive-stress layer on its surface.

Meanwhile, JP-A-2009-167086 discloses a cover glass for mobile terminalsthat exhibits high strength even at a thin glass substrate and that canthus reduce the thickness of the device on which the cover glass ismounted.

The aforementioned cover glass is produced as follows. First, a resistpattern is formed on the principal surfaces of a plate-shaped glasssubstrate. Then, with the resist pattern serving as a mask, the glasssubstrate is etched with an etchant which consists of a mixed-acidaqueous solution containing hydrofluoric acid and at least one type ofacid selected from sulfuric acid, nitric acid, hydrochloric acid, andhydrofluorosilicic acid, to thereby cut the glass substrate into adesired shape. Then, the etched glass substrate is subjected to chemicalstrengthening by an ion-exchange process. With this method, it ispossible to produce a cover glass having end surfaces that have asurface roughness of 10 nm or less in arithmetic mean roughness (Ra).

According to the aforementioned method, it is possible to produce achemically-strengthened cover glass having complicated shapes withnegative curvatures and/or through-holes by etching the plate-shapedglass substrate into predetermined shapes. In the above method, theprocessing time required for etching takes up a large proportion of theoverall shape-processing step and has a huge impact on the cover-glassproduction efficiency. It is therefore important to shorten theprocessing time required for etching.

Further, in the chemical etching process of the aforementioned method,poorly-soluble chemical substances elute into the etchant, whichcontains hydrofluoric acid, and adhere to the glass substrate. This notonly impairs the surface quality of the etched cover glass, but alsoinhibits the progress of the etching process if large amounts ofchemical substances adhere to the glass surface, which may extend theprocessing time and impair the accuracy in shape.

SUMMARY

An object of the present disclosure is to provide a method for producingcover glasses with which the cover-glass production efficiency can beimproved by increasing the etching rate, and to provide cover glassesproduced thereby. Another object of the present disclosure is to providea method for producing cover glasses with which cover glasses havingcomplicated shapes can be produced with high shape accuracy, and toprovide cover glasses produced thereby.

An aspect of the present invention relates to a method for producing acover glass. The method involves:

a step of subjecting a glass substrate to shape-processing by etching,the glass substrate having been formed into a plate-like shape by adown-drawing process and containing, as components thereof, 50% to 70%by mass of SiO₂, 5% to 20% by mass of Al₂O₃, 6% to 30% by mass of Na₂O,and 0% to less than 8% by mass of Li₂O; and

a step of forming a compressive-stress layer on the shape-processedglass substrate by subjecting the glass substrate to chemicalstrengthening.

Another aspect of the present invention relates to a method forproducing a cover glass. The method involves:

a step of subjecting a glass substrate to shape-processing, the glasssubstrate having been formed into a plate-like shape and containing, ascomponents thereof, 50% to 70% by mass of SiO₂, 5% to 20% by mass ofAl₂O₃, 6% to 30% by mass of Na₂O, 0% to less than 8% by mass of Li₂O,and 0% to 2.6% by mass of CaO;

a step of processing at least an end surface of the shape-processedglass substrate by chemical etching; and

a step of forming a compressive-stress layer on the processed glasssubstrate by subjecting the glass substrate to chemical strengthening.

Another aspect of the present invention relates to a cover glass. Thecover glass is a plate-shaped glass substrate that has been formed intoa plate-like shape by a down-drawing process, that has been subjected toshape-processing by etching, and that has been chemically strengthenedso as to have a compressive-stress layer on the principal surfacesthereof.

The glass substrate contains, as components thereof, 50% to 70% by massof SiO₂, 5% to 20% by mass of Al₂O₃, 6% to 30% by mass of Na₂O, and 0%to less than 8% by mass of Li₂O.

The glass substrate has an etching characteristic in which an etchingrate is at least 3.7 μm/minute in an etching environment having atemperature of 22° C. and containing hydrogen fluoride with aconcentration of 10% by mass.

Another aspect of the present invention relates to a cover glass. Thecover glass is a plate-shaped glass substrate that has been subjected toshape-processing by etching and that has been chemically strengthened soas to have a compressive-stress layer on the principal surfaces thereof.

The glass substrate contains, as components thereof, 50% to 70% by massof SiO₂, 5% to 20% by mass of Al₂O₃, 6% to 30% by mass of Na₂O, 0% toless than 8% by mass of Li₂O, and 0% to 2.6% by mass of CaO.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 illustrates an example of a cover glass according to anembodiment of the disclosure.

FIG. 2 is a cross-sectional view of the cover glass illustrated in FIG.1 taken along line A-A′ therein.

FIG. 3 is a chart illustrating the relationship between various glasscompositions and etching rates according to the first embodiment.

FIGS. 4A and 4B illustrate how to evaluate the processing accuracy ofglass-plate etching.

FIGS. 5A and 5B illustrate examples of observation images of glassplates taken with an optical microscope.

FIG. 6 is a chart illustrating the relationship between various glasscompositions and etching rates according to the second embodiment.

DESCRIPTION OF THE EMBODIMENTS

Cover glasses and methods for producing the same of the presentdisclosure will be described in detail below in accordance with firstand second embodiments thereof. Note that the term “percentage (percent;%)” (or content by percentage) as used herein to indicate the content ofeach component constituting the glass refers to percentage by mass (mass%) unless stated otherwise.

A cover glass, as described in the first and second embodiments, is usedfor protecting the display screen of equipment such as mobile phones,digital cameras, PDAs, and FPDs. However, the cover glasses of the firstand second embodiments are not limited to the aforementionedapplications, and can also be employed, for example, as substrates fortouch-panel displays, substrates for magnetic disks, cover glasses forsolar batteries, and window panes. According to the first embodiment,the etching rate can be increased, thus improving the cover-glassproduction efficiency. The second embodiment allows cover glasses withhigh shape accuracy to be produced in addition to improving thecover-glass production efficiency, thus further improving thecover-glass production efficiency.

Cover Glass According to First Embodiment

FIG. 1 illustrates a piece of cover glass 10 as an example of thepresent embodiment. The cover glass 10 illustrated in FIG. 1 hasrecesses 12 formed in the right and left sides (in the figure) of apiece of plate-shaped glass. In the cover glass 10, some sections ofeach recess 12 have negative curvatures as defined above. The coverglass 10 is also provided with a slit-form hole 14. The edge surroundingthe hole 14 has sections with negative curvatures as defined above.

FIG. 2 is a cross-sectional view of the cover glass 10 of FIG. 1 takenin the direction of arrows A-A′. The cover glass 10 has acompressive-stress layer 16 formed on the principal surfaces thereof andalso on the end surfaces thereof. The compressive-stress layer 16 can beformed on the end surfaces of the cover glass 10 as well as theprincipal surfaces by the cover glass 10 being subjected to a chemicalstrengthening process after shape-processing.

More specifically, the cover glass 10 is prepared by first subjecting adown-drawn glass substrate to shape-processing by etching, and thensubjecting the etched glass substrate to chemical strengthening by anion-exchange process. The glass substrate contains, as its components,50% to 70% of SiO₂, 5% to 20% of Al₂O₃, 6% to 30% of Na₂O, and 0% toless than 8% of Li₂O. Further, the glass substrate has an etchingcharacteristic in which the etching rate is at least 3.7 μm/minute in anetching environment having a temperature of 22° C. and containinghydrogen fluoride with a concentration of 10% by mass.

The composition of the glass substrate constituting the cover glass 10will be described in detail below.

Composition of Glass Substrate According to First Embodiment

The glass substrate to be used for the cover glass 10 in the firstembodiment contains SiO₂, Al₂O₃, and Na₂O, and may also contain B₂O₃,Li₂O, K₂O, MgO, CaO, SrO, BaO, ZnO, ZrO₂, TiO₂, P₂O₅, SnO₂, and SO₃, ifnecessary.

SiO₂:

SiO₂ is an essential component that constitutes the skeletal structureof the glass to be used for the glass substrate, and has the effect ofimproving the chemical durability and heat resistance of the glass. Ifthe SiO₂ content by percentage is less than 50%, vitrification maybecome difficult and sufficient effects in durability and heatresistance may not be obtained, although the etching rate at the time ofetching the glass substrate to perform shape-processing thereon tends toimprove. On the other hand, if the SiO₂ content by percentage exceeds70%, then the glass is likely to cause devitrification and the glassmaterials will become hard to melt and form, and also, the viscositywill increase and the glass will become hard to homogenize, therebyposing difficulty in mass-producing glass inexpensively by usingdown-drawing processes. Further, if the content by percentage exceeds70%, the coefficient of thermal expansion will become too small and willless likely match the coefficients of thermal expansion of peripheralmaterials such as metals and organic adhesives. Furthermore, if thecontent by percentage exceeds 70%, the low-temperature viscosity willincrease excessively and thus the ion-exchange rate will drop, resultingin that sufficient strength cannot be achieved even with chemicalstrengthening through ion exchange. Therefore, the content by percentageof SiO₂ is from 50% to 70%, preferably from 53% to 67%, more preferablyfrom 53% to 65%, even more preferably from 55% to 65%, and particularlypreferably from 58% to 63%. Note that the low-temperature viscosityrefers to the temperature at 10^(7.6) to 10^(14.5) dPa·s, but in thepresent embodiment, it is defined as indicating the temperature at10^(14.5) dPa·s.

Al₂O₃:

Al₂O₃ is an essential component that constitutes the skeletal structureof the glass to be used for the glass substrate, and has the effect ofimproving the chemical durability and heat resistance of the glass andof improving the ion-exchange performance and the etching rate at thetime of performing shape-processing by etching. If the Al₂O₃ content bypercentage is less than 5%, the aforementioned effects cannot beobtained sufficiently. On the other hand, if the Al₂O₃ content bypercentage exceeds 20%, the glass will become hard to melt and also theviscosity of the glass will increase, which will make it hard to form.Thus, it becomes difficult to mass-produce glass inexpensively by usingdown-drawing processes. Further, if the Al₂O₃ content by percentageexceeds 20%, the acid resistance will become excessively poor, which isnot preferable for a cover glass. Furthermore, if the Al₂O₃ content bypercentage exceeds 20%, the glass is likely to cause devitrification andthe devitrification resistance will deteriorate as well, which will makedown-draw processing inapplicable. Therefore, the content by percentageof Al₂O₃ is from 5% to 20%, preferably from 5% to 17%, more preferablyfrom 7% to 16%, and particularly preferably from 9% to 15%.

Note that in the present embodiment, it is preferable that, if thecontent by percentage of SiO₂ is X % and the content by percentage ofAl₂O₃ is Y %, X−1/2·Y is 57.5% or less. In cases where X−1/2·Y is 57.5%or less, the etching rate of the glass substrate can be improvedeffectively. The range for X−1/2·Y is more preferably 56% or less, andeven more preferably 55% or less.

On the other hand, if the range for X−1/2·Y is below 45%, thedevitrification temperature will rise and thus the devitrificationresistance will deteriorate, although the etching rate will reach 5μm/minute or higher. Therefore, in order to achieve both an improvementin devitrification resistance and an improvement in etching rate, therange for X−1/2·Y is preferably 45% or greater, more preferably 47% orgreater, and particularly preferably 50% or greater. Specifically, therange for X−1/2·Y is preferably 45% to 57.5%, more preferably 47% to56%, and even more preferably 50% to 55%.

B₂O³:

B₂O₃ is a component that decreases the viscosity of the glass and thatpromotes the melting and refining of the glass to be used for the glasssubstrate. If the content by percentage exceeds 5%, the acid resistanceof the glass will deteriorate and also the amount of volatilization willincrease, thereby making the glass hard to homogenize. Also, theincrease in the amount of volatilization will cause unevenness in thecomponents of the glass and will also cause unevenness in the etching onthe glass substrate. That is, the etching rate will become uneven amongthe various areas of the glass, and therefore, a glass substratecontaining an excessive amount of B₂O₃ is not suitable for purposes suchas etching with the aim of shape-processing, which requires highaccuracy. Further, if the B₂O₃ content by percentage exceeds 5%, thenthe strain point will be lowered, thus making the glass deform at thetime of subjecting the glass substrate to thermal processing. Therefore,the B₂O₃ content by percentage is preferably from 0% to 5%, morepreferably from 0% to 3%, even more preferably from 0% to less than 2%,and particularly preferably less than 0.01% and B₂O₃ shouldintentionally not be contained except for impurities. By adjusting theB₂O₃ content by percentage to 0% to 5%, it is possible to achieve theeffect of improving the etching rate and also prevent unevenness inetching, thereby allowing the production of cover glasses with higherquality.

Li₂O:

Li₂O is one of the ion-exchange components and is a component thatreduces the viscosity of the glass to be used for the glass substrateand that improves the meltability and formability of the glass. Li₂O isalso a component that improves the Young's modulus of the glasssubstrate, and among various alkali metal oxides, Li₂O is highlyeffective in increasing the stress value of the compressive-stresslayer. However, if the Li₂O content by percentage is too large, therewill be a disadvantage that the ion-exchange salts will deteriorate toosoon in the ion-exchange process, which is the step of strengthening theglass substrate, thereby leading to an increase in the production costof the cover glass. Further, if the Li₂O content by percentage is toolarge, then the coefficient of thermal expansion of the glass willbecome too large and the thermal shock resistance thereof willdeteriorate, and also the coefficient of thermal expansion will lesslikely match the coefficients of thermal expansion of peripheralmaterials such as metals and organic adhesives. Furthermore, if the Li₂Ocontent by percentage is too large, then not only will the heatresistance deteriorate, but also the low-temperature viscosity will dropexcessively; this will cause stress relaxation in the heating step afterchemical strengthening and will reduce the stress value of thecompressive-stress layer, resulting in not being able to produce a coverglass with sufficient strength. Therefore, the Li₂O content bypercentage is from 0% to less than 8%, preferably from 0% to 5%, morepreferably from 0% to 2%, even more preferably from 0% to 1%, furthermore preferably from 0% to 0.02%, and desirably less than 0.01%, and itis particularly preferable that Li₂O is intentionally not containedexcept for impurities.

Na₂O:

Na₂O is one of the ion-exchange components and is an essential componentthat reduces the high-temperature viscosity of the glass to be used forthe glass substrate and that improves the meltability and formability ofthe glass. Further, Na₂O is a component that improves thedevitrification resistance of the glass. If the Na₂O content bypercentage is less than 6%, the meltability of the glass willdeteriorate, which will increase the cost for melting. Further, if theNa₂O content by percentage is less than 6%, then the ion-exchangeperformance will also deteriorate, resulting in that sufficient strengthcannot be achieved. Furthermore, if the Na₂O content by percentage isless than 6%, then the coefficient of thermal expansion will be toosmall and will less likely match the coefficients of thermal expansionof peripheral materials such as metals and organic adhesives. Moreover,if the Na₂O content by percentage is less than 6%, the glass is likelyto cause devitrification and the devitrification resistance willdeteriorate as well, which will make down-draw processing inapplicableand thereby pose difficulty in mass-producing glass inexpensively. Onthe other hand, if the Na₂O content by percentage exceeds 30%, then thelow-temperature viscosity will drop and the impact resistance willdeteriorate, and also the coefficient of thermal expansion will be toolarge and will less likely match the coefficients of thermal expansionof peripheral materials such as metals and organic adhesives. Further,if the Na₂O content by percentage exceeds 30%, also the devitrificationresistance will deteriorate due to the loss of balance in the glass,thereby posing difficulty in mass-producing glass inexpensively by usingdown-drawing processes. Therefore, the Na₂O content by percentage isfrom 6% to 30%, preferably from 7% to 27%, more preferably from 10% to20%, even more preferably from 12% to 20%, and particularly preferablyfrom 13% to 19%.

Further, in the present embodiment, the difference found by subtractingthe Al₂O₃ content by percentage from the Na₂O content by percentage(“Na₂O content percentage−Al₂O₃ content percentage”) is preferably from−10% to 15%. When the difference “Na₂O content percentage−Al₂O₃ contentpercentage” is within the range of −10% to 15%, then not only can thecover-glass production efficiency be improved, but also the meltabilityof the glass can be improved while keeping the coefficient of thermalexpansion and heat resistance at a suitable level. Therefore, the glasscan be molten at lower temperatures, thereby allowing further reductionsin the cost for producing the cover glass. Note that the range for thedifference “Na₂O content percentage−Al₂O₃ content percentage” is morepreferably from −5% to 13%, even more preferably from −5% to 10%, andfurther more preferably from −3% to 5%.

K₂O:

K₂O is one of the ion-exchange components and is a component that canimprove the ion-exchange performance of the glass substrate by beingincluded therein. K₂O also reduces the high-temperature viscosity of theglass, improves the meltability and formability thereof, and alsoimproves the devitrification resistance. However, if the K₂O content bypercentage is too large, the low-temperature viscosity will drop, thecoefficient of thermal expansion will become too large, and the impactresistance will become poor, which is not preferable for a cover glass.Further, if the K₂O content by percentage is too large, the coefficientof thermal expansion will less likely match the coefficients of thermalexpansion of peripheral materials such as metals and organic adhesives.Furthermore, if the K₂O content by percentage is too large, also thedevitrification resistance will deteriorate due to the loss of balancein the glass, thereby posing difficulty in mass-producing glassinexpensively by using down-drawing processes. Therefore, the K₂Ocontent by percentage is 15% or less, preferably 10% or less, morepreferably less than 5.6%, even more preferably less than 5%, andparticularly preferably less than 4%. On the other hand, the lower limitof the K₂O content by percentage is 0% or greater, preferably 0.1% orgreater, more preferably 1% or greater, and even more preferably 2% orgreater. Adjusting the lower limit of the K₂O content by percentage tobe within the aforementioned range not only improves the etching rate,but can also shorten the time required for ion-exchange processing andimprove the cover glass productivity. Specifically, the content percentof K₂O is preferably 0% to 15%, preferably 0.1% to 10%, more preferably1% to less than 5.6%, even more preferably 2% to less than 5%, andparticularly preferably 2% to less than 4%.

R¹ ₂O (R¹ includes all the elements among Li, Na, and K that arecontained in the glass substrate):

In the present embodiment, the R¹ ₂O content by percentage is preferablyfrom 6% to 30%. If the percentage of R¹ ₂O is less than 6%, ion exchangewill not be performed sufficiently and thus a sufficient strength cannotbe obtained, thereby posing difficulty in using the glass substrate fora cover glass. On the other hand, if the percentage of R¹ ₂O exceeds30%, the devitrification temperature will be increased due to the lossof balance in the glass, which will make down-draw processing hard toemploy and thereby pose difficulty in mass-producing glassinexpensively. In order to achieve both mechanical strength anddevitrification resistance and to improve productivity, the R¹ ₂Ocontent by percentage is more preferably from 10% to 28%, even morepreferably from 14% to 25%, further more preferably from 15% to 24%, andparticularly preferably from 17% to 23%.

Note that the aforementioned range for the content by percentage of R¹₂O is a criterion to be satisfied in addition to each range of contentby percentage as set forth above for the oxide of each of the elementsamong Li, Na, and K contained in the glass substrate.

B₂O₃/R¹ ₂O (R¹ includes all the elements among Li, Na, and K that arecontained in the glass substrate):

In the present embodiment, the ratio in content by percentage betweenB₂O₃ and R¹ ₂O (“B₂O₃/R¹ ₂O”) is preferably from 0 to less than 0.3.B₂O₃ is prone to bond with an alkali metal oxide and volatilize as analkali borate, and particularly, Li⁺, which has a small ionic radius,has high mobility in the glass melt and is prone to volatilize from thesurface of the melt, and volatilization is likely to create aconcentration gradient up to the inner part of the glass and to giverise to striae on the surface of the glass. In other words, an increasein the amount of volatilization of B₂O₃ will make the produced glasssubstrate nonuniform, and unevenness in etching will occur due to thenonuniformity of the glass substrate when such a glass substrate issubjected to etching. However, alkali metal oxides are essentialcomponents to glass that is chemically strengthened by an ion-exchangeprocess. Therefore, the ratio B₂O₃/R¹ ₂O in content by percentage (theratio in percentage by mass) is preferably adjusted to be within therange of 0 to less than 0.3. In this range, the nonuniformity of theglass and unevenness in etching can be reduced effectively. Thus, notonly is the etching rate improved, but also unevenness in etching ratecan be prevented, thereby allowing strengthened glass of desired shapeto be produced with high yield. Note that the range for the ratioB₂O₃/R¹ ₂O in content by percentage is more preferably from 0 to 0.1,even more preferably from 0 to 0.07, further preferably from 0 to 0.03,even more preferably from 0 to 0.005, and particularly preferably 0.Further, in order to reduce unevenness in etching, it is most preferablethat the Li₂O content by percentage is less than 0.01% and Li₂O shouldintentionally not be contained except for impurities, as describedabove.

MgO:

MgO is a component that decreases the viscosity of the glass to be usedfor the glass substrate and that promotes the melting and refining ofthe glass. Also, among alkaline-earth metals, MgO is an effectivecomponent for improving the meltability while making the glasslightweight, because it only increases the glass density by a smallrate. MgO also improves formability and increases the strain point andYoung's modulus of the glass. Furthermore, the rate at whichcrystallized products are produced at the time of etching MgO-containingglass by using e.g. hydrofluoric acid is relatively low, and therefore,it is relatively less likely for the crystallized products to adhere tothe glass surface during etching. Thus, it is preferable to include MgOin order to improve the glass meltability and to increase the etchingrate. However, if the MgO content is too large, then the devitrificationresistance will deteriorate, thus posing difficulty in mass-producingglass inexpensively by using down-drawing processes. Therefore, the MgOcontent by percentage is from 0% to 15%, preferably greater than 1% to15%, more preferably greater than 1% to 12%, further preferably greaterthan 1% to less than 7%, even more preferably from 3% to less than 7%,and particularly preferably greater than 4.5% to 6%. The inclusion ofMgO within the range of 0% to 15% will improve the etching rate and willalso allow the glass to be molten at lower temperatures, therebyallowing further reductions in the cost for producing the cover glass.Furthermore, because it is possible to improve the ion-exchangeperformance and increase the strain point at the same time, theMgO-containing glass is suitable for cover glasses that require highmechanical strength. This is because a sufficient compressive-stresslayer can be formed on the surface of the glass substrate, and thecompressive-stress layer formed on the surface can be prevented fromcausing stress relaxation, even during/after thermal treatment.

CaO:

CaO is a component that decreases the viscosity of the glass to be usedfor the glass substrate and that promotes the melting and refining ofthe glass. Also, among alkaline-earth metals, CaO is an effectivecomponent for improving the meltability while making the glasslightweight, because it only increases the glass density by a smallrate. CaO also improves formability and increases the strain point andYoung's modulus of the glass. However, if the CaO content is too large,then the devitrification resistance will deteriorate, thus posingdifficulty in mass-producing glass inexpensively by using down-drawingprocesses. Also, if the CaO content is too large, the ion-exchangeperformance will deteriorate; thus, sufficient strength cannot beachieved, and also productivity will be reduced. Further, thecrystallized products produced at the time of subjecting glass thatcontains large amounts of CaO to wet-etching by using e.g. hydrofluoricacid are not only insoluble in the etchant solution, but are produced atan extremely high precipitation rate. Therefore, such crystallizedproducts adhere to the surface of the glass being etched, and if theadherence amount is large, the etching reaction will be inhibited andthe glass-processing quality will be impaired. On the other hand, theinclusion of CaO can lower the devitrification temperature and improvethe devitrification resistance and meltability. Therefore, the CaOcontent by percentage is from 0% to 10%, preferably from 0% to 8%, morepreferably from 0% to 6%, even more preferably from 0% to 4%, andparticularly preferably from 0% to 2%. Note that in cases where anextremely-high etching quality is required, it is preferable thatsubstantially no CaO is contained.

Further, it is even more preferable to include both MgO and CaO in orderto reduce the melt viscosity and at the same time lower thedevitrification temperature, but the amount of CaO shall be adjusted asappropriate to fall within the range that will not give rise to theaforementioned problems caused by the crystallized products producedduring etching.

SrO:

SrO is a component that decreases the viscosity of the glass to be usedfor the glass substrate and that promotes the melting and refining ofthe glass. SrO also improves formability and increases the strain pointand Young's modulus of the glass. However, if the SrO content is toolarge, then the glass density will increase, and the glass will beunsuitable for cover glasses, which are required to be lightweight.Further, if the SrO content is too large, then the coefficient ofthermal expansion will be too large and will less likely match thecoefficients of thermal expansion of peripheral materials such as metalsand organic adhesives. Furthermore, if the SrO content is too large,then the ion-exchange performance will also deteriorate, making itdifficult to obtain the high mechanical strength demanded of coverglasses. Therefore, the SrO content by percentage is preferably from 0%to 10%, more preferably from 0% to 5%, even more preferably from 0% to2%, and further more preferably from 0% to 0.5%, and it is particularlypreferable that SrO is intentionally not contained except forimpurities.

BaO:

BaO is a component that decreases the viscosity of the glass to be usedfor the glass substrate and that promotes the melting and refining ofthe glass. BaO also improves formability and increases the strain pointand Young's modulus of the glass. However, if the BaO content is toolarge, then the glass density will increase, and the glass will beunsuitable for cover glasses, which are required to be lightweight.Further, if the BaO content is too large, then the coefficient ofthermal expansion will be too large and will less likely match thecoefficients of thermal expansion of peripheral materials such as metalsand organic adhesives. Furthermore, if the BaO content is too large,then the ion-exchange performance will also deteriorate, making itdifficult to obtain the high mechanical strength demanded of coverglasses. Therefore, the BaO content by percentage is preferably from 0%to 10%, more preferably from 0% to 5%, even more preferably from 0% to2%, and further more preferably from 0% to 0.5%. Note that, because BaOplaces a heavy burden on the environment, it is particularly preferablethat the BaO content is less than 0.01% and BaO should intentionally notbe contained except for impurities.

SrO+BaO:

In the present embodiment, the sum found by adding the SrO content bypercentage and the BaO content by percentage (“SrO contentpercentage+BaO content percentage”) is preferably less than 10%. Whenthe sum “SrO content percentage+BaO content percentage” is less than10%, it is possible to effectively prevent an increase in the glassdensity and a decrease in the ion-exchange rate. That is, adjusting thesum “SrO content percentage+BaO content percentage” to less than 10%will not only improve the etching rate, but can also achieve the effectof making the cover glass lightweight and the effect of improvingproductivity and glass strength. Note that the range for the sum “SrOcontent percentage+BaO content percentage” is preferably from 0% to 8%,more preferably from 0% to 5%, even more preferably from 0% to 2%, andfurther more preferably from 0% to 1%, and it is particularly preferablethat SrO and BaO are intentionally not contained except for impurities.

RO (R includes all the elements among Mg, Ca, Sr, and Ba that arecontained in the glass substrate):

Herein, the RO content by percentage is preferably from 0% to 20%. Ifthe RO content is greater than 20%, the chemical durability willdeteriorate. On the other hand, the inclusion of RO can improve themeltability and heat resistance of the glass. Therefore, the RO contentby percentage is preferably from 0% to 10%, more preferably from 0% to7%, even more preferably from 2% to 7%, further preferably from 3% to7%, and further more preferably from 4% to 7%.

Note that the aforementioned range for the content by percentage of ROis a criterion to be satisfied in addition to each range of content bypercentage as set forth above for the oxide of each of the elementsamong Mg, Ca, Sr, and Ba contained in the glass substrate.

Li₂O/(RO+Li₂O):

In the present embodiment, the ratio in content by percentage betweenLi₂O and the sum of RO and Li₂O (“Li₂O/(RO+Li₂O)”; wherein R includes atleast one type of element selected from Mg, Ca, Sr, and Ba) ispreferably less than 0.3. In this way, it is possible to inhibit thedeterioration of ion-exchange salts in the ion-exchange process, whichis the step of strengthening the glass substrate, and it is thuspossible to reduce the cost for producing the strengthened glass to beused as the cover glass. Further, if the ratio “Li₂O/(RO+Li₂O)” incontent by percentage is less than 0.3, the devitrification temperaturecan be lowered effectively, and thus, the devitrification resistance canbe improved effectively. Further, if the ratio “Li₂O/(RO+Li₂O)” incontent by percentage is less than 0.3, then the strain point can beincreased effectively and also the heat resistance can be improved. Thatis, adjusting the ratio “Li₂O/(RO+Li₂O)” in content by percentage toless than 0.3 not only increases the etching rate, but can also improvethe heat resistance and prevent such problems as stress relaxationduring chemical strengthening and the deformation of glass during otherthermal treatments. Note that the range for the ratio “Li₂O/(RO+Li₂O)”in content by percentage is more preferably 0.08 or less, even morepreferably 0.05 or less, further more preferably 0.01 or less, andparticularly preferably 0.

ZnO:

ZnO is a component that improves the ion-exchange performance, that ishighly effective particularly in improving the compressive-stress value,and that lowers the high-temperature viscosity of the glass withoutlowering the low-temperature viscosity. However, if the ZnO content istoo large, the glass will cause phase separation and the devitrificationresistance will deteriorate. Further, if the ZnO content is too large,then the glass density will increase, and the glass will be unsuitablefor cover glasses, which are required to be lightweight. Therefore, theZnO content by percentage is preferably from 0% to 6%, more preferablyfrom 0% to 4%, even more preferably from 0% to 1%, further morepreferably from 0% to 0.1%, and particularly preferably less than 0.01%and ZnO should intentionally not be contained except for impurities.

ZrO₂:

ZrO₂ is a component that significantly improves the ion-exchangeperformance and that increases the strain point and the viscosity nearthe devitrification temperature of the glass. Further, ZrO₂ improves theheat resistance of the glass. However, if the ZrO₂ content is too large,the devitrification temperature will be increased and thedevitrification resistance will deteriorate. Therefore, in order toprevent a reduction in devitrification resistance, the ZrO₂ content bypercentage is preferably from 0% to 15%, more preferably from 0% to 10%,even more preferably from 0% to 6% or less, and further more preferablyfrom 0% to 4% or less. By including ZrO₂, it is possible to effectivelyimprove heat resistance, which is important for cover glasses used inmobile phones and for cover glasses used in touch-panel displays, and toeffectively improve ion-exchange performance, which relates to thereduction of time for chemically strengthening the glass substrate andto the improvement of the mechanical strength thereof. Therefore, theZrO₂ content by percentage is preferably 0.1% or greater, morepreferably 0.5% or greater, even more preferably 1% or greater, andparticularly preferably 2% or greater. That is, by adjusting the ZrO₂content by percentage to 0.1% or greater, the heat resistance andion-exchange performance can be improved while also improvingdevitrification resistance. Thus, the time required for ion-exchangeprocessing can be reduced, and thus productivity can be improved. It isalso possible to prevent the glass from deforming during the chemicalstrengthening process and other thermal treatments, and thus the yieldof cover glasses can be enhanced.

On the other hand, if the glass density is to be reduced, then the ZrO₂content by percentage should preferably be less than 0.1%, and it isparticularly preferable that ZrO₂ is intentionally not contained exceptfor impurities.

TiO₂:

TiO₂ is a component that improves the ion-exchange performance and thatreduces the high-temperature viscosity of the glass. However, if theTiO₂ content is too large, the devitrification resistance willdeteriorate. Further, if the TiO₂ content is too large, then the UVtransmittance will deteriorate and the glass will be stained, which isnot suitable for cover glasses or the like. Furthermore, if the TiO₂content is too large, then the UV transmittance will deteriorate, thuscausing a disadvantage that, in the case of using a UV-curable resin,the resin cannot be cured sufficiently. Therefore, the TiO₂ content bypercentage is preferably from 0% to 5%, more preferably from 0% to lessthan 3%, even more preferably from 0% to 1%, and further more preferablyfrom 0% to 0.01%, and it is particularly preferable that TiO₂ isintentionally not contained except for impurities.

(ZrO₂+TiO₂)/SiO₂:

In the present embodiment, the ratio in content by percentage betweenthe sum of ZrO₂ and TiO₂ to SiO₂ (“(ZrO₂+TiO₂)/SiO₂”) is preferably from0% to 0.2%. In the case of shape-processing a glass substrate byetching, ion-exchange processing will be performed after etching. In theion-exchange process, deformation may occur due to the internal stresswithin the glass substrate if ion exchange is carried out excessively.In other words, excessive ion exchange gives rise to the deformation ofthe glass substrate, and thus the shape that has been processed withhigh accuracy by etching cannot be retained and the glass substratebecomes unsuitable for a cover glass. So, by adjusting the ratio“(ZrO₂+TiO₂)/SiO₂” in content by percentage to be within the range of 0to 0.2 excessive ion exchange can be inhibited effectively. Note thatthe range for the ratio “(ZrO₂+TiO₂)/SiO₂” in content by percentage ispreferably from 0 to 0.15, more preferably from 0 to 0.1, even morepreferably from 0 to 0.07, and particularly preferably from 0 to 0.01.When the ratio “(ZrO₂+TiO₂)/SiO₂” in content by percentage is within therange of 0 to 0.2, the devitrification resistance as well as the heatresistance can be improved while preventing excessive ion exchange.

P₂O₅:

P₂O₅ is a component that improves the ion-exchange performance and thatis highly effective particularly in increasing the thickness of thecompressive-stress layer. However, if the P₂O₅ content is too large, theglass will cause phase separation and the water resistance willdeteriorate. Therefore, the P₂O₅ content by percentage is preferablyfrom 0% to 10%, more preferably from 0% to 4%, even more preferably from0% to 1%, further more preferably from 0% to 0.1%, and particularlypreferably less than 0.01% and P₂O₅ should intentionally not becontained except for impurities.

In addition to the aforementioned components, the glass substratecontains refining agents as described below.

Refining Agent:

A refining agent is a component necessary for the refining of the glassto be used for the glass substrate. No refining effect can be obtainedif the content is less than 0.001%, whereas the content exceeding 5% maycause devitrification and/or staining. Therefore, the total content bypercentage of refining agent(s) is preferably from 0.001% to 5%, morepreferably from 0.01% to 3%, even more preferably from 0.05% to 1%, andparticularly preferably from 0.05% to 0.5%.

The refining agents are not particularly limited as far as they havelittle burden on the environment and provide the glass with excellentclarity. Examples include one or more types of agents selected from thegroup of oxides of metals including, for example, Sn, Fe, Ce, Tb, Mo,and W.

The following ranges are preferable for the metal oxides, the oxidesbeing expressed as SnO₂, Fe₂O₃, and CeO₂.

SnO₂ is a component that is prone to devitrify the glass. So, in orderto prevent devitrification while improving the clarity, it is preferablethat the SnO₂ content by percentage is from 0% to 0.5%, more preferablyfrom 0.01% to 0.5%, even more preferably from 0.05% to 0.3%, and furthermore preferably from 0.1% to 0.2%.

Fe₂O₃ is a component that stains the glass. So, in order to achieve asuitable transmittance while improving the clarity, it is preferablethat the Fe₂O₃ content by percentage is from 0% to 0.2%, more preferablyfrom 0.01% to 0.2%, even more preferably from 0.05% to 0.15%, andfurther more preferably from 0.05% to 0.10%. Note that, particularly incases where transparency and UV transmission characteristics aredemanded of the glass, it is preferable that the Fe₂O₃ content is lessthan 0.02%, and particularly preferable that Fe₂O₃ is intentionally notcontained except for impurities.

The CeO₂ content by percentage is preferably from 0% to 1.2%, morepreferably from 0.01% to 1.2%, even more preferably from 0.05% to 1.0%,and particularly preferably from 0.3% to 1.0%.

Further, in cases where particularly high transmittance is demanded ofglass, such as in a cover glass, it is desirable to employ SO₃ as therefining agent. It is preferable that the SO₃ content by percentage isfrom 0% to 5%, preferably from 0.001% to 5%, more preferably from 0.01%to 3%, even more preferably from 0.05% to 1%, further more preferablyfrom 0.05% to 0.5%, and particularly preferably from 0.05% to 0.20%. Inthe case of employing SO₃ as the refining agent, the combined use in themelting step of carbon and a sulfate, such as sodium sulfate, serving asthe source of SO₃ can achieve an even higher refining effect. Note thatSO₃ can be used in combination with other refining agents, as describedabove.

As₂O₃, Sb₂O₃, and PbO also have the effect of refining glass by causingreactions that involve a change in valance in molten glass. However,these compounds place a heavy burden on the environment. Therefore, inthe glass substrate of the present embodiment, the amount of thesecompounds is limited so that As₂O₃, Sb₂O₃, and PbO are substantially notincluded in the glass. Note that, herein, the expression “As₂O₃, Sb₂O₃,and PbO are substantially not included” means that the content is lessthan 0.01% and that these compounds are intentionally not includedexcept for impurities.

Oxides of rare-earth elements, such as Nb₂O₅ and La₂O₃, are componentsthat increase the Young's modulus of the glass to be used for the glasssubstrate. However, if the content of these compounds is too large, thedevitrification resistance will deteriorate. Therefore, the content bypercentage of rare-earth oxides, such as Nb₂O₅ and La₂O₃, is preferably3% or less, more preferably 1% or less, even more preferably 0.5% orless, and particularly preferably less than 0.1% and these compoundsshould intentionally not be included except for impurities.

Note that in the present embodiment, components that stain the glass,such as Co and Ni, are not preferable because such components reduce thetransmittance of the glass substrate or the strengthened glass obtainedafter ion-exchange processing. In the case of touch-panel displays, forexample, a reduction in the transmittance of the glass substrate or thestrengthened glass is not preferable because the visibility of thetouch-panel display will be impaired. Therefore, the content oftransition metal elements that stain the glass, such as Co and Ni, ispreferably 1% or less, more preferably 0.5% or less, even morepreferably 0.05% or less, and particularly preferably less than 0.05%and such compounds should intentionally not be included except forimpurities.

Method for Producing Cover Glass According to First Embodiment

The method for producing a cover glass according to the presentembodiment will be described below. The cover-glass production methodinvolves the following steps (1) to (4):

(1) a step of melting glass materials in which the components have beenformulated and blended so as to provide the glass substrate with theaforementioned composition;

(2) a step of forming the molten glass, which has been molten in themelting step, into a plate-like shape by a down-draw process;

(3) a step of subjecting the plate-like shaped glass to shape-processingby etching; and

(4) a step of forming a compressive-stress layer on the surfaces of theshape-processed glass by subjecting the glass to chemical strengthening.

The down-draw process used in Step (2) above includes such processes asthe overflow down-draw process and the slot down-draw process. Amongthem, the overflow down-draw process is suitably used.

Step (1):

Step (1) is the step of melting glass materials in which the componentshave been formulated and blended so as to provide the glass substratewith the aforementioned glass composition.

More specifically, the glass materials corresponding to theaforementioned components are measured and blended, are placed in amelting pot made, for example, of fire brick, platinum, or a platinumalloy, where they are heated and molten, and then are subjected torefining and homogenization, thereby preparing molten glass having adesired composition.

Step (2):

Step (2) is the step of forming the molten glass having the desiredcomposition, which has been prepared in Step (1), into a plate-likeshape by a down-draw process. The down-draw process is a known processdisclosed, for example, in JP-A-2009-203080. In the down-draw process,molten glass is fed into a trough which is provided on a forming bodyand is made to flow over both sides of the trough. The overflowed moltenglass flows downward along both the side surfaces of the forming bodyhaving a wedge-shaped cross section and located below the trough,creating two flows of molten glass which join at the lowermost end ofthe forming body. The joining of the two flows results in a strip ofglass, which is drawn by drawing rollers provided below the formingbody. Thus, the molten glass is formed into a strip of glass having apredetermined thickness.

There are various processes for forming glass into a plate-like shape,including various down-draw processes, the float process, the re-drawprocess, and the roll-out process. The present embodiment employs thedown-draw process, because glass substrates formed by using thedown-draw process are improved in etching rate, as compared to otherforming processes such as the float process. Another reason is that theprincipal surfaces of a glass substrate formed by using the down-drawprocess are extremely smooth, because they are made by hot forming.

More specifically, in the case of shape-processing the aforementionedglass substrate by etching, the glass substrate can be etched evenlyfrom both the principal surfaces thereof at the time of etching theglass substrate from the principal surfaces thereof that have resistpatterns thereon serving as masks. In other words, the uniformcomposition of the glass substrate enhances the dimensional accuracy inetching and also improves the sectional shape of the end surfaces of thecover glass, which may be used in a mobile phone, a touch-panel display,etc.

Also, both the principal surfaces of the glass substrate formed by usingthe down-draw process have a uniform composition, and therefore, therewill be no difference in the ion-exchange rate between the principalsurfaces during the later-described ion-exchange process. Thus, theglass substrate can be prevented from warping after ion exchange due toa difference in composition. In other words, it becomes possible toproduce homogeneous cover glasses, to improve productivity, and toreduce costs.

Further, forming the glass by using the down-draw process can do awaywith the polishing step after forming, thus further reducing costs andimproving productivity. Also, forming by using the down-draw process canproduce glass substrates with surfaces having no microcracks, which, inturn, can improve the strength of the glass substrates.

Step (3):

Step (3) is the step of subjecting the plate-shaped glass substrate toshape-processing by etching, to process the glass substrate into adesired shape.

The following explains how the cover glass is subjected toshape-processing by etching prior to the ion-exchange processing step.

First, both the principal surfaces of the plate-shaped glass substrateprepared as above are coated with a resist material. Then, the resistmaterial is exposed via a photo mask having a desired outer-shapepattern. The outer shape is not particularly limited, and it may be anouter shape including, for example, sections having negative curvatures,as illustrated in FIG. 1.

Next, the exposed resist material is developed to thus form a resistpattern on the glass substrate in regions other than theregions-to-be-etched, and then, the regions-to-be-etched on the glasssubstrate are etched. If a wet etchant is used as the etchant, the glasssubstrate will be etched isotropically. Thus, each end surface of theglass substrate will be formed so as to have: a central section thatprojects outward the most; and sloped faces that curve gently from thecentral section toward the respective principal surfaces. It ispreferable that the boundaries between the sloped faces and therespective principal surfaces and the boundary between the two slopedfaces are rounded.

The resist material to be used in the etching step is not particularlylimited, and it is possible to use a material that is resistant to theetchant used for etching the glass while using the resist pattern as amask. For example, glass is, in general, corroded by wet etching usingan aqueous solution containing hydrofluoric acid or by dry etching usinga fluorine-based gas, so resist materials having excellent resistance tohydrofluoric acid are suitable. As for the etchant, it is possible tosuitably use a mixed acid containing at least one of hydrofluoric acid,sulfuric acid, nitric acid, hydrochloric acid, and hydrofluorosilicicacid. The use of hydrofluoric acid or the aforementioned mixed-acidaqueous solution as the etchant can produce cover glasses with desiredshapes.

Further, even complicated outer shapes can be created easily, just byadjusting the mask pattern at the time of performing shape-processing byemploying etching. Further, performing shape-processing through etchingcan further improve productivity and also cut down processing costs. Asfor the stripping solution for stripping the resist material off fromthe glass substrate, an alkaline solution such as KOH or NaOH may beused. The type of resist material, etchant, and stripping solution canbe selected as appropriate depending on the material of the glasssubstrate.

Note that the etching process is not limited to the process of simplyimmersing the glass substrate into an etching solution, but instead itis possible to employ, for example, spray etching in which the etchingsolution is sprayed.

By subjecting the glass substrate to shape-processing by employingetching as described above, it is possible to produce a cover glasshaving end surfaces with a highly-smooth surface roughness. Morespecifically, it is possible to prevent microcracks, which areinevitably created in shape-processing that employs machining, and tothus further improve the mechanical strength of the cover glass.

The glass substrate of the present embodiment has an etchingcharacteristic in which the etching rate is at least 3.7 μm/minute in anetching environment having a temperature of 22° C. and containinghydrogen fluoride with a concentration of 10% by mass. The above etchingcharacteristic can be achieved by adjusting the composition of the glasssubstrate in a manner such that, if the content of the aforementionedSiO₂ is X % and the content of the aforementioned Al₂O₃ is Y %, X−1/2·Yis 57.5% or less.

Step (4):

Step (4) is the step of subjecting the glass substrate shape-processedin Step (3) to an ion-exchange process.

The cover glass according to the present embodiment is produced byperforming an ion-exchange process on the glass substrate that has beenshape-processed in Step (3) as described above. More specifically, forexample, after being rinsed, the glass substrate is immersed for around1 to 25 hours in a treatment bath containing 100% of KNO₃ and kept ataround 350° C. to 550° C., to thereby exchange the Na⁺ ions on thesuperficial layer of the glass with K⁺ ions present in the treatmentbath. In this way, the glass substrate can be chemically strengthened.Note that the temperature, the length of time, the ion-exchangesolution, etc., for the ion-exchange process can be changed asappropriate. For example, the ion-exchange solution may be a mixedsolution containing two or more types of compounds.

The foregoing was a description on the cover glass of the firstembodiment.

Next, the cover glass according to the second embodiment will bedescribed below. The glass substrate to be used in the cover glass ofthe second embodiment is a preferable embodiment of the glass substrateaccording to the first embodiment, in that the content by percentage ofCaO has been limited. This limitation not only improves the etching rateduring etching, which is performed as the shape-processing step, as inthe first embodiment, but can also provide the end surfaces of the glasswith uniform etching surfaces—i.e., can improve the processing accuracy.

Cover Glass According to Second Embodiment

As with the cover glass of the first embodiment, the cover glassaccording to the second embodiment also has the shape and features asillustrated in FIG. 1. As illustrated in FIG. 1, the cover glass 100 ofthe second embodiment has recesses 102 formed in the right and leftsides (in the figure) of a piece of plate-shaped glass. Some sections ofeach recess 102 have negative curvatures as defined above. The coverglass 100 is also provided with a slit-form hole 104. The edgesurrounding the hole 104 has sections with negative curvatures asdefined above.

As illustrated in FIG. 2, the cover glass 100 has a compressive-stresslayer 106 formed on the principal surfaces thereof and also on the endsurfaces thereof. The compressive-stress layer 106 can be formed on theend surfaces of the cover glass 100 as well as the principal surfaces bythe cover glass 100 being subjected to a chemical strengthening processafter shape-processing.

More specifically, the cover glass 100 is prepared by first subjecting aglass substrate that has been formed into a plate-like shape by adown-draw process, to shape-processing by a processing techniqueincluding chemical etching, and then subjecting the shape-processedglass substrate to chemical strengthening by an ion-exchange process.The glass substrate contains, as its components, 50% to 70% of SiO₂, 5%to 20% of Al₂O₃, 6% to 30% of Na₂O, 0% to less than 8% of Li₂O, and 0%to 2.6% of CaO. The content by percentage of CaO is preferably 1.5% orless, more preferably 1.0% or less, even more preferably 0.2% or less,and it is particularly preferable that substantially no CaO is included.Herein, the expression “substantially no CaO is included” means that thecontent is less than 0.01% and CaO is intentionally not included exceptfor impurities. Further, the glass substrate has an etchingcharacteristic in which the etching rate is at least 3.7 μm/minute in anetching environment having a temperature of 22° C. and containinghydrogen fluoride with a concentration of 10% by mass.

The composition of the glass substrate constituting the cover glass 100will be described in detail below.

Composition of Glass Substrate According to Second Embodiment

The glass substrate to be used for the cover glass 100 contains SiO₂,Al₂O₃, and Na₂O, and may also contain B₂O₃, Li₂O, K₂O, MgO, CaO, SrO,BaO, ZnO, ZrO₂, TiO₂, P₂O₅, SnO₂, and SO₃, if necessary. In thefollowing, the essential components refer to components that need to beincluded in the glass substrate, whereas the optional components referto components that do not have to be included at all in the glasssubstrate.

SiO₂:

SiO₂ is an essential component that constitutes the skeletal structureof the glass to be used for the glass substrate, and has the effect ofimproving the chemical durability and heat resistance of the glass. Ifthe SiO₂ content by percentage is less than 50%, vitrification maybecome difficult and sufficient effects in durability and heatresistance may not be obtained, although the etching rate at the time ofetching the glass substrate to perform shape-processing thereon tends toimprove. On the other hand, if the SiO₂ content by percentage exceeds70%, then the glass is likely to cause devitrification and the glassmaterials will become hard to melt and form, and also, the viscositywill increase and the glass will become hard to homogenize, therebyposing difficulty in mass-producing glass inexpensively by usingdown-drawing processes. Further, if the content by percentage exceeds70%, the coefficient of thermal expansion will become too small and willless likely match the coefficients of thermal expansion of peripheralmaterials such as metals and organic adhesives. Furthermore, if thecontent by percentage exceeds 70%, the low-temperature viscosity willincrease excessively and thus the ion-exchange rate will drop, resultingin that sufficient strength cannot be achieved even with chemicalstrengthening through ion exchange. Therefore, the content by percentageof SiO₂ is from 50% to 70%, preferably from 53% to 67%, more preferablyfrom 55% to 67%, even more preferably from 58% to 65%, and particularlypreferably from 60% to 65%. Note that low-temperature viscosity refersto the temperature at 10^(7.6) to 10^(14.5) dPa·s, but in the presentembodiment, it is defined as indicating the temperature at 10^(14.5)dPa·s.

Al₂O₃:

Al₂O₃ is an essential component that constitutes the skeletal structureof the glass to be used for the glass substrate, and has the effect ofimproving the chemical durability and heat resistance of the glass andof improving the ion-exchange performance and the etching rate at thetime of performing shape-processing by etching. If the Al₂O₃ content bypercentage is less than 5%, the aforementioned effects cannot beobtained sufficiently. On the other hand, if the Al₂O₃ content bypercentage exceeds 20%, the glass will become hard to melt and also theviscosity of the glass will increase, which will make it hard to form.Thus, it becomes difficult to mass-produce glass inexpensively by usingdown-drawing processes. Further, if the Al₂O₃ content by percentageexceeds 20%, the acid resistance will become excessively poor, which isnot preferable for a cover glass which is used as a protectivecomponent. Furthermore, if the Al₂O₃ content by percentage exceeds 20%,the glass is likely to cause devitrification and the devitrificationresistance will deteriorate as well, which will make down-drawprocessing inapplicable. Therefore, the content by percentage of Al₂O₃is from 5% to 20%, preferably from 5% to 17%, more preferably from 7% to16%, and particularly preferably from 9% to 15%.

Note that in the present embodiment, it is preferable that, if thecontent by percentage of SiO₂ is X % and the content by percentage ofAl₂O₃ is Y %, X−1/2·Y is 57.5% or less. When X−1/2·Y is 57.5% or less,the etching rate of the glass substrate can be improved effectively. Thepreferable range for X−1/2. Y is more preferably 56% or less, and evenmore preferably 55% or less.

On the other hand, if X−1/2·Y is below 45%, the devitrificationtemperature will rise and thus the devitrification resistance willdeteriorate, although the etching rate will reach 5 μm/minute or higher.Therefore, in order to achieve both an improvement in devitrificationresistance and an improvement in etching rate, X−1/2·Y is preferably 45%or greater, more preferably 47% or greater, and particularly preferably50% or greater. Specifically, the range for X−1/2·Y is preferably 45% to57.5%, more preferably 47% to 56%, and even more preferably 50% to 55%.

B₂O₃:

B₂O₃ is an optional component that decreases the viscosity of the glassand that promotes the melting and refining of the glass to be used forthe glass substrate. If the content by percentage exceeds 5%, the acidresistance of the glass will deteriorate and also volatilization willincrease, thereby making the glass hard to homogenize. Also, theincrease in volatilization will cause unevenness in the glass and willalso cause unevenness in the etching on the glass substrate. That is,the etching rate will become uneven among the various areas of theglass, and therefore, a glass substrate containing an excessive amountof B₂O₃ is not suitable for purposes such as etching with the aim ofshape-processing, which requires high accuracy. Therefore, the B₂O₃content by percentage is preferably from 0% to 5%, more preferably from0% to 3%, even more preferably from 0% to less than 2%, and particularlypreferably less than 0.01% and B₂O₃ should intentionally not becontained except for impurities. By adjusting the B₂O₃ content bypercentage to 0% to 5%, it is possible to achieve the effect ofimproving the etching rate and also prevent unevenness in etching,thereby allowing the production of cover glasses with higher quality.

Li₂O:

Li₂O is one of the ion-exchange components and is an optional componentthat reduces the viscosity of the glass to be used for the glasssubstrate and that improves the meltability and formability of theglass. Li₂O is also a component that improves the Young's modulus of theglass substrate, and among various alkali metal oxides, Li₂O is highlyeffective in increasing the depth of the compressive-stress layer.However, if the Li₂O content by percentage is too large, there will be adisadvantage that the ion-exchange salts will deteriorate too soon inthe ion-exchange process, which is the step of strengthening the glasssubstrate, thereby leading to an increase in the production cost of thecover glass. Furthermore, if the Li₂O content by percentage is toolarge, then not only will the heat resistance deteriorate excessively(the strain point and the glass transition point drop excessively), butalso the low-temperature viscosity will drop excessively; this willcause stress relaxation in the heating step after chemical strengtheningand will reduce the stress value of the compressive-stress layer,resulting in not being able to produce a cover glass with sufficientstrength. Therefore, the Li₂O content by percentage is from 0% to lessthan 8%, preferably from 0% to 5%, more preferably from 0% to 2%, evenmore preferably from 0% to 1%, further more preferably from 0% to 0.02%,and desirably less than 0.01%, and it is particularly preferable thatLi₂O is intentionally not contained except for impurities.

Meanwhile, if the strain point and the glass transition point become toohigh, it becomes necessary to increase the temperature for theion-exchange process optimal for ensuring a compressive-stress layerhaving predetermined characteristics that would match the glasscomposition. However, if the ion-exchange processing temperature becomestoo high, then the ion-exchange processing temperature may exceed thedecomposition temperature of the ion-exchange salts. Incidentally, Li₂Ocan effectively reduce the molten glass transition point and the strainpoint, so the ion-exchange processing temperature can be reduced byincreasing the content by percentage of Li₂O. However, if the Li₂Ocontent becomes too large, then it becomes difficult to observe fringepatterns in the ion-exchanged strengthened glass that are related to therefractive index, thus making it difficult to measure the stress valueand the thickness of the compressive-stress layer with a stress meterwhile retaining the shape of the strengthened glass. Therefore, if it isdesired to facilitate the measurement of the compressive-stress layerand at the same time reduce the ion-exchange processing temperature,then it is preferable to adjust the content by percentage of Li₂O togreater than 0%—i.e., to include Li₂O in the glass composition—and morepreferably to 0.001% or greater, even more preferably to 0.01% orgreater, and further more preferably to 0.02% or greater. Also, the Li₂Ocontent is suitably 1.3% or less, preferably less than 0.5%, morepreferably less than 0.4%, even more preferably 0.3% or less, andparticularly preferably 0.2% or less. Specifically, the contentpercentage of Li₂O is preferably 0.001% to 1.3%, more preferably 0.01%to less than 0.5%, even more preferably 0.02% to less than 0.4%, furthermore preferably 0.02% to 0.3%, and particularly preferably 0.02% to0.2%.

Na₂O:

Na₂O is one of the ion-exchange components and is an essential componentthat reduces the high-temperature viscosity of the glass to be used forthe glass substrate and that improves the meltability and formability ofthe glass. Further, Na₂O is a component that improves thedevitrification resistance of the glass. If the Na₂O content bypercentage is less than 10%, the meltability of the glass willdeteriorate, which will increase the cost for melting. Further, if theNa₂O content by percentage is less than 10%, then the ion-exchangeperformance will also deteriorate, resulting in that sufficient strengthcannot be achieved. Furthermore, if the Na₂O content by percentage isless than 10%, then the coefficient of thermal expansion will be toosmall and will less likely match the coefficients of thermal expansionof peripheral materials such as metals and organic adhesives. Moreover,if the Na₂O content by percentage is less than 10%, the glass is likelyto cause devitrification and the devitrification resistance willdeteriorate as well, which will make down-draw processing inapplicableand thereby pose difficulty in mass-producing glass inexpensively. Onthe other hand, if the Na₂O content by percentage exceeds 25%, then thelow-temperature viscosity will drop and the impact resistance willdeteriorate, and also the coefficient of thermal expansion will be toolarge and will less likely match the coefficients of thermal expansionof peripheral materials such as metals and organic adhesives. Therefore,the Na₂O content by percentage is from 6% to 30%, preferably from 10% to25%, more preferably from 10% to 20%, even more preferably from 12% to20%, and particularly preferably from 13% to 19%.

Further, in the present embodiment, the difference found by subtractingthe Al₂O₃ content by percentage from the Na₂O content by percentage(“Na₂O content percentage−Al₂O₃ content percentage”) is preferably from−10% to 15%. When the difference “Na₂O content percentage−Al₂O₃ contentpercentage” is within the range of −10% to 15%, then not only can theobjects described in the present disclosure be achieved, but also themeltability of the glass can be improved while keeping the coefficientof thermal expansion and heat resistance at a suitable level. Therefore,the glass can be molten at lower temperatures, thereby allowing furtherreductions in the cost for producing the cover glass. Note that therange for the difference “Na₂O content percentage−Al₂O₃ contentpercentage” is more preferably from −5% to 13%, even more preferablyfrom −5% to 10%, and further more preferably from −3% to 5%.

K₂O:

K₂O is an optional component that can improve the ion-exchangeperformance of the glass substrate by being included therein. K₂O alsoreduces the high-temperature viscosity of the glass, improves themeltability and formability thereof, and also improves thedevitrification resistance. However, if the K₂O content is too large,the low-temperature viscosity will drop, the coefficient of thermalexpansion will become too large, and the impact resistance will becomepoor, which is not preferable for a cover glass. Further, if the K₂Ocontent by percentage is too large, the coefficient of thermal expansionwill less likely match the coefficients of thermal expansion ofperipheral materials such as metals and organic adhesives. Therefore,the K₂O content by percentage is 15% or less, preferably 10% or less,more preferably less than 5.6%, even more preferably less than 5%, andparticularly preferably less than 4%. On the other hand, the lower limitof the K₂O content by percentage is 0% or greater, preferably 0.1% orgreater, more preferably 1% or greater, and even more preferably 2% orgreater. Adjusting the lower limit of the K₂O content by percentage tobe within the aforementioned range not only improves the etching rate,but can also shorten the time required for ion-exchange processing andimprove the cover glass productivity. Specifically, the content percentof K₂O is preferably 0% to 15%, more preferably 0.1% to 10%, even morepreferably 1% to less than 5.6%, further more preferably 2% to less than5%, and particularly preferably 2% to less than 4%.

R¹ ₂O (R¹ includes all the elements among Li, Na, and K that arecontained in the glass substrate):

In the present embodiment, the R¹ ₂O content by percentage (the totalcontent by percentage of all the elements among Li, Na, and K that arecontained in the glass substrate) is preferably from 6% to 30%. If thepercentage of R¹ ₂O is less than 6%, ion exchange will not be performedsufficiently and thus a sufficient strength cannot be obtained, therebyposing difficulty in using the glass substrate for a cover glass. On theother hand, if the percentage of R¹ ₂O exceeds 30%, the chemicaldurability of the glass will deteriorate. So, in order to achieve bothmechanical strength and devitrification resistance and to improvechemical durability and productivity, the R¹ ₂O content by percentage ismore preferably from 10% to 28%, even more preferably from 14% to 25%,further more preferably from 15% to 24%, and particularly preferablyfrom 17% to 23%.

Note that the aforementioned range for the content by percentage of R¹₂O is a criterion to be satisfied in addition to each range of contentby percentage as set forth above for the oxide of each of the elementsamong Li, Na, and K contained in the glass substrate.

B₂O₃/R¹ ₂O (R¹ includes all the elements among Li, Na, and K that arecontained in the glass substrate):

In the present embodiment, the ratio in content by percentage betweenB₂O₃ and R¹ ₂O (“B₂O₃/R¹ ₂O”) is preferably from 0 to less than 0.3.B₂O₃ is prone to bond with an alkali metal oxide and volatilize as analkali borate, and particularly, Li⁺, which has a small ionic radius,has high mobility in the glass melt and is prone to volatilize from thesurface of the melt, and volatilization is likely to create aconcentration gradient up to the inner part of the glass and to giverise to striae on the surface of the glass. In other words, an increasein the amount of volatilization of B₂O₃ will make the produced glasssubstrate nonuniform, and unevenness in etching will occur due to thenonuniformity of the glass substrate when such a glass substrate issubjected to etching. However, alkali metal oxides are essentialcomponents to glass that is chemically strengthened by an ion-exchangeprocess. Therefore, the ratio B₂O₃/R¹ ₂O in content by percentage (theratio in percentage by mass) is preferably adjusted to be within therange of 0 to less than 0.3. In this range, the nonuniformity of theglass and unevenness in etching can be reduced effectively. Thus, notonly is the etching rate improved, but also unevenness in etching ratecan be prevented, thereby allowing strengthened glass of desired shapeto be produced with high yield. Note that the range for the ratioB₂O₃/R¹ ₂O in content by percentage is more preferably from 0 to 0.1,preferably from 0 to 0.07, more preferably from 0 to 0.03, even morepreferably from 0 to 0.005, and particularly preferably 0. Further, inorder to reduce unevenness in etching, it is preferable that the Li₂Ocontent by percentage is less than 0.01% and Li₂O should intentionallynot be contained except for impurities, as described above.

MgO:

MgO is an optional component that decreases the viscosity of the glassto be used for the glass substrate and that promotes the melting andrefining of the glass. Also, among alkaline-earth metals, MgO is aneffective component for improving the meltability while making the glasslightweight, because it only increases the glass density by a smallrate. MgO also improves formability and increases the strain point andYoung's modulus of the glass. Furthermore, the precipitations that areproduced at the time of etching MgO-containing glass by using e.g.hydrofluoric acid have large solubility and relatively low productionrate, and therefore, it is relatively less likely for the precipitationsto adhere to the glass surface during etching. Thus, it is preferable toinclude MgO in order to improve the glass meltability and to increasethe etching rate. However, if the MgO content is too large, then thedevitrification resistance will deteriorate, thus posing difficulty inmass-producing glass inexpensively by using down-drawing processes.Therefore, the MgO content by percentage is from 0% to 15%, preferablygreater than 1% to 15%, more preferably greater than 1% to 12%, furtherpreferably greater than 1% to less than 7%, even more preferably from 3%to less than 7%, and particularly preferably greater than 4.5% to 6%.The inclusion of MgO within the range of 0% to 15% will improve theetching rate and will also allow the glass to be molten at lowertemperatures, thereby allowing further reductions in the cost forproducing the cover glass. Furthermore, because it is possible toimprove the ion-exchange performance and increase the strain point atthe same time, the MgO-containing glass is suitable for cover glassesthat require high mechanical strength. This is because a sufficientcompressive-stress layer can be formed on the surface of the glasssubstrate, and the compressive-stress layer formed on the surface can beprevented from causing stress relaxation, even during/after thermaltreatment.

CaO:

CaO is an optional component that decreases the viscosity of the glassto be used for the glass substrate and that promotes the melting andrefining of the glass. Also, among alkaline-earth metals, CaO is aneffective component for improving the meltability while making the glasslightweight, because it only increases the glass density by a smallrate. CaO also improves formability and increases the strain point andYoung's modulus of the glass. However, if the CaO content is too large,then the devitrification resistance will deteriorate, thus posingdifficulty in mass-producing glass inexpensively by using down-drawingprocesses. Also, if the CaO content is too large, the ion-exchangeperformance will deteriorate; thus, sufficient strength cannot beachieved, and also productivity will be reduced. Further, theprecipitations (chemical substances) produced at the time of subjectingglass that contains large amounts of CaO to wet-etching by using e.g.hydrofluoric acid are not only insoluble in the etchant solution, butalso are produced at an extremely high precipitation rate. Therefore,such precipitations adhere to the surface of the glass being etched, andif the adherence amount is large, the etching reaction will beinhibited, the glass-processing productivity will be impaired, and alsothe glass surface after etching will be degraded. In other words, theinclusion of CaO will not only degrade the surface quality of the etchedcover glass, but may also inhibit the progress of etching if largeamounts of precipitations adhere to the glass surface, which may extendthe etching time and deteriorate the shape accuracy (processingaccuracy). On the other hand, the inclusion of CaO can lower thedevitrification temperature and improve the devitrification resistanceand meltability. Therefore, the CaO content by percentage is from 0% to2.6%, preferably from 0% to 1.5%, more preferably from 0% to 1.0%, evenmore preferably from 0% to 0.6%, and further more preferably from 0% to0.2%. Note that in cases where an extremely-high etching quality isrequired, it is preferable that substantially no CaO is contained.

Further, it is even more preferable to include both MgO and CaO in orderto reduce the melt viscosity and at the same time lower thedevitrification temperature, but the amount of CaO shall be adjusted asappropriate to fall within the range that will not give rise to theaforementioned problems caused by the precipitations formed duringetching. Therefore, the upper limit of the content by percentage of CaOis 2.6%.

SrO:

SrO is an optional component that decreases the viscosity of the glassto be used for the glass substrate and that promotes the melting andrefining of the glass. SrO also improves formability and increases thestrain point and Young's modulus of the glass. However, if the SrOcontent is too large, then the glass density will increase, and theglass will be unsuitable for cover glasses, which are required to belightweight. Further, if the SrO content is too large, then thecoefficient of thermal expansion will be too large and will less likelymatch the coefficients of thermal expansion of peripheral materials suchas metals and organic adhesives. Furthermore, if the SrO content is toolarge, then the ion-exchange performance will also deteriorate, makingit difficult to obtain the high mechanical strength demanded of coverglasses. Therefore, the SrO content by percentage is preferably from 0%to 10%, more preferably from 0% to 5%, even more preferably from 0% to2%, and further more preferably from 0% to 0.5%, and it is particularlypreferable that SrO is intentionally not contained except forimpurities.

BaO:

BaO is an optional component that decreases the viscosity of the glassto be used for the glass substrate and that promotes the melting andrefining of the glass. BaO also improves formability and increases thestrain point and Young's modulus of the glass. However, if the BaOcontent is too large, then the glass density will increase, and theglass will be unsuitable for cover glasses, which are required to belightweight. Further, if the BaO content is too large, then thecoefficient of thermal expansion will be too large and will less likelymatch the coefficients of thermal expansion of peripheral materials suchas metals and organic adhesives. Furthermore, if the BaO content is toolarge, then the ion-exchange performance will also deteriorate, makingit difficult to obtain the high mechanical strength demanded of coverglasses. Therefore, the BaO content by percentage is preferably from 0%to 10%, more preferably from 0% to 5%, even more preferably from 0% to2%, and further more preferably from 0% to 0.5%. Note that, because BaOplaces a heavy burden on the environment, it is particularly preferablethat the BaO content is less than 0.01% and BaO should intentionally notbe contained except for impurities.

SrO+BaO:

In the present embodiment, the sum found by adding the SrO content bypercentage and the BaO content by percentage (“SrO contentpercentage+BaO content percentage”) is preferably less than 10%. Whenthe sum “SrO content percentage+BaO content percentage” is less than10%, it is possible to effectively prevent an increase in the glassdensity and a decrease in the ion-exchange rate. That is, adjusting thesum “SrO content percentage+BaO content percentage” to less than 10%will not only improve the etching rate, but can also achieve the effectof making the cover glass lightweight and the effect of improvingproductivity and glass strength. Note that the range for the sum “SrOcontent percentage+BaO content percentage” is preferably from 0% to 8%,more preferably from 0% to 5%, even more preferably from 0% to 2%, andfurther more preferably from 0% to 1%, and it is particularly preferablethat SrO and BaO are intentionally not contained except for impurities.

RO (R includes all the elements among Mg, Ca, Sr, and Ba that arecontained in the glass substrate):

Herein, the RO content by percentage (the total content by percentage ofall the elements among Mg, Ca, Sr, and Ba that are contained in theglass substrate) is preferably from 0% to 20%. If the RO content isgreater than 20%, the chemical durability will deteriorate. On the otherhand, the inclusion of RO can improve the meltability and heatresistance of the glass. Therefore, the RO content by percentage ispreferably from 0% to 10%, more preferably from 0% to 7%, even morepreferably from 2% to 7%, further preferably from 3% to 7%, and furthermore preferably from 4% to 7%.

Note that the aforementioned range for the content by percentage of ROis a criterion to be satisfied in addition to each range of content bypercentage as set forth above for the oxide of each of the elementsamong Mg, Ca, Sr, and Ba contained in the glass substrate.

Li₂O/(RO+Li₂O):

In the present embodiment, the ratio in content by percentage betweenLi₂O and the sum of RO and Li₂O (“Li₂O/(RO+Li₂O)”; wherein R includesall the elements selected from Mg, Ca, Sr, and Ba that are contained inthe glass substrate) is preferably less than 0.3. By adjusting the ratioLi₂O/(RO+Li₂O) in content by percentage to be within the aforementionedrange, it is possible to inhibit the deterioration of ion-exchange saltsin the ion-exchange process, which is the step of strengthening theglass substrate, and it is thus possible to reduce the cost forproducing the strengthened glass to be used as the cover glass. Further,if the ratio “Li₂O/(RO+Li₂O)” in content by percentage is less than 0.3,the devitrification temperature can be lowered effectively, and thus,the devitrification resistance can be improved effectively. Further, ifthe ratio “Li₂O/(RO+Li₂O)” in content by percentage is less than 0.3,then the strain point can be increased effectively and also the heatresistance can be improved. That is, such a content by percentage notonly increases the etching rate, but can also improve the heatresistance and prevent such problems as stress relaxation duringchemical strengthening. Note that the range for the ratio“Li₂O/(RO+Li₂O)” in content by percentage is more preferably 0.08 orless, even more preferably 0.05 or less, further more preferably 0.01 orless, and particularly preferably 0.

ZnO:

ZnO is an optional component that improves the ion-exchange performance,that is highly effective particularly in improving thecompressive-stress value, and that lowers the high-temperature viscosityof the glass without lowering the low-temperature viscosity. However, ifthe ZnO content is too large, the glass will cause phase separation andthe devitrification resistance will deteriorate. Further, if the ZnOcontent is too large, then the glass density will increase, and theglass will be unsuitable for cover glasses, which are required to belightweight. Therefore, the ZnO content by percentage is preferably from0% to 6%, more preferably from 0% to 4%, even more preferably from 0% to1%, further more preferably from 0% to 0.1%, and particularly preferablyless than 0.01% and ZnO should intentionally not be contained except forimpurities.

ZrO₂:

ZrO₂ is an optional component that significantly improves theion-exchange performance and that increases the strain point and theviscosity near the devitrification temperature of the glass. Further,ZrO₂ improves the heat resistance of the glass. However, if the ZrO₂content is too large, the devitrification temperature will be increasedand the devitrification resistance will deteriorate. Therefore, in orderto prevent a reduction in devitrification resistance, the ZrO₂ contentby percentage is preferably from 0% to 10%, more preferably from 0% to6% or less, even more preferably from 0% to 4% or less, and further morepreferably from 0% to 2% or less. By including ZrO₂, it is possible toeffectively improve heat resistance, which is important for coverglasses used in mobile phones and for cover glasses used in touch-paneldisplays, and to effectively improve ion-exchange performance, whichrelates to the reduction of time for chemically strengthening the glasssubstrate and to the improvement of the mechanical strength thereof.Therefore, the ZrO₂ content by percentage is preferably 0.1% or greater,more preferably 0.5% or greater, even more preferably 1% or greater, andparticularly preferably 2% or greater. That is, by adjusting the ZrO₂content by percentage to 0.1% or greater, the heat resistance andion-exchange performance can be improved while also improvingdevitrification resistance. Thus, the time required for ion-exchangeprocessing can be reduced, and thus productivity can be improved.

On the other hand, if the glass density is to be reduced, then the ZrO₂content by percentage should preferably be less than 0.1%, and it isparticularly preferable that ZrO₂ is intentionally not contained exceptfor impurities.

TiO₂:

TiO₂ is an optional component that improves the ion-exchange performanceand that reduces the high-temperature viscosity of the glass. However,if the TiO₂ content is too large, the devitrification resistance willdeteriorate. Further, if the TiO₂ content is too large, then the UVtransmittance will deteriorate and the glass will be stained, which isnot suitable for cover glasses or the like. Furthermore, if the TiO₂content is too large, then the UV transmittance will deteriorate, thuscausing a disadvantage that, in the case of using a UV-curable resin,the resin cannot be cured sufficiently. Therefore, the TiO₂ content bypercentage is preferably from 0% to 5%, more preferably from 0% to lessthan 3%, even more preferably from 0% to 1%, and further more preferablyfrom 0% to 0.01%, and it is particularly preferable that TiO₂ isintentionally not contained except for impurities.

(ZrO₂+TiO₂)/SiO₂:

In the present embodiment, the ratio in content by percentage betweenthe sum of ZrO₂ and TiO₂ to SiO₂ (“(ZrO₂+TiO₂)/SiO₂”) is preferably from0 to 0.2. In the case of shape-processing a glass substrate by etching,ion-exchange processing will be performed after etching. In theion-exchange process, deformation may occur due to the internal stresswithin the glass substrate if ion exchange is carried out excessively.In other words, excessive ion exchange gives rise to the deformation ofthe glass substrate, and thus the shape that has been processed withhigh accuracy by etching cannot be retained and the glass substratebecomes unsuitable for a cover glass. So, by adjusting the ratio“(ZrO₂+TiO₂)/SiO₂” in content by percentage to be within the range of 0to 0.2, excessive ion exchange can be inhibited effectively. Note thatthe range for the ratio “(ZrO₂+TiO₂)/SiO₂” in content by percentage ispreferably from 0 to 0.15, more preferably from 0 to 0.1, even morepreferably from 0 to 0.07, and particularly preferably from 0 to 0.01.When the ratio “(ZrO₂+TiO₂)/SiO₂” in content by percentage is within therange of 0 to 0.2, the devitrification resistance as well as the heatresistance can be improved while preventing excessive ion exchange.

P₂O₅:

P₂O₅ is an optional component that improves the ion-exchange performanceand that is highly effective particularly in increasing the thickness ofthe compressive-stress layer. However, if the P₂O₅ content is too large,the glass will cause phase separation and the water resistance willdeteriorate. Therefore, the P₂O₅ content by percentage is preferablyfrom 0% to 10%, more preferably from 0% to 4%, even more preferably from0% to 1%, further more preferably from 0% to 0.1%, and particularlypreferably less than 0.01% and P₂O₅ should intentionally not becontained except for impurities.

In addition to the aforementioned components, the glass substratecontains refining agents as described below.

Refining Agent:

A refining agent is a component necessary for the refining of the glassto be used for the glass substrate. No refining effect can be obtainedif the content is less than 0.001%, whereas the content exceeding 5% maycause devitrification and/or staining. Therefore, the total content bypercentage of refining agent(s) is preferably from 0.001% to 2%, morepreferably from 0.01% to 1%, even more preferably from 0.05% to 0.5%,and particularly preferably from 0.05% to 0.2%.

The refining agents are not particularly limited as far as they havelittle burden on the environment and provide the glass with excellentclarity. Examples include one or more types of agents selected from thegroup of oxides of metals including, for example, Sn, Fe, Ce, Tb, Mo,and W.

The following ranges are preferable for the metal oxides, the oxidesbeing expressed as SnO₂, Fe₂O₃, and CeO₂.

SnO₂ is a component that is prone to devitrify the glass. So, in orderto prevent devitrification while improving the clarity, it is preferablethat the SnO₂ content by percentage is from 0% to 0.5%, more preferablyfrom 0.01% to 0.5%, even more preferably from 0.05% to 0.3%, and furthermore preferably from 0.1% to 0.2%.

Fe₂O₃ is a component that stains the glass. So, in order to achieve asuitable transmittance while improving the clarity, it is preferablethat the Fe₂O₃ content by percentage is from 0% to 0.2%, more preferablyfrom 0.01% to 0.2%, even more preferably from 0.05% to 0.15%, andfurther more preferably from 0.05% to 0.10%. Note that, particularly incases where transparency and UV transmission characteristics aredemanded of the glass, it is preferable that the Fe₂O₃ content is lessthan 0.02%, and particularly preferable that Fe₂O₃ is intentionally notcontained except for impurities.

The CeO₂ content by percentage is preferably from 0% to 1.2%, morepreferably from 0.01% to 1.2%, even more preferably from 0.05% to 1.0%,and particularly preferably from 0.3% to 1.0%.

Further, for cover glasses that require a particularly hightransmittance, it is desirable to employ SO₃ as the refining agent. Itis preferable that the SO₃ content by percentage is from 0% to 5%,preferably from 0.001% to 5%, more preferably from 0.01% to 3%, evenmore preferably from 0.05% to 1%, further more preferably from 0.05% to0.5%, and particularly preferably from 0.05% to 0.20%. In the case ofemploying SO₃ as the refining agent, the combined use in the meltingstep of carbon and a sulfate, such as sodium sulfate, serving as thesource of SO₃ can achieve an even higher refining effect. Note that SO₃can be used in combination with other refining agents, as describedabove.

As₂O₃ and Sb₂O₃ also have the effect of refining glass by causingreactions that involve a change in valance in molten glass. However,these compounds place a heavy burden on the environment. Therefore, inthe glass substrate of the present embodiment, the amount of thesecompounds is limited so that As₂O₃ and Sb₂O₃ are substantially notincluded in the glass. Note that, herein, the expression “As₂O₃ andSb₂O₃ are substantially not included” means that the content is lessthan 0.01% and that these compounds are intentionally not includedexcept for impurities. Further, PbO and F have the effect of improvingthe glass meltability and refining the glass. However, these compoundsplace a heavy burden on the environment. Therefore, in the cover glassof the present embodiment, it is preferable that PbO and F aresubstantially not included in the glass.

Oxides of rare-earth elements, such as Nb₂O₅ and La₂O₃, are optionalcomponents that increase the Young's modulus of the glass to be used forthe glass substrate. However, if the content of these compounds is toolarge, the devitrification resistance will deteriorate. Therefore, thecontent by percentage of rare-earth oxides, such as Nb₂O₅ and La₂O₃, ispreferably 3% or less, more preferably 1% or less, even more preferably0.5% or less, and particularly preferably less than 0.1% and thesecompounds should intentionally not be included except for impurities.

Note that in the present embodiment, components that stain the glass,such as Co and Ni, are not preferable because such components reduce thetransmittance of the glass substrate or the strengthened glass obtainedafter ion-exchange processing. In the case of touch-panel displays, forexample, a reduction in the transmittance of the glass substrate or thestrengthened glass is not preferable because the visibility of thetouch-panel display will be impaired. Therefore, the content oftransition metal elements that stain the glass, such as Co and Ni, ispreferably 1% or less, more preferably 0.5% or less, even morepreferably 0.05% or less, and particularly preferably less than 0.05%and such compounds should intentionally not be included except forimpurities.

Method for Producing Cover Glass According to Second Embodiment

The method for producing a cover glass according to the presentembodiment will be described below. The cover-glass production methodinvolves the following steps (1) to (4):

(1) a step of melting glass materials in which the components have beenformulated and blended so as to provide the glass substrate with theaforementioned composition;

(2) a step of forming the molten glass, which has been molten in themelting step, into a plate-like shape;

(3) a step of subjecting the plate-like shaped glass substrate toshape-processing by a processing technique including at least chemicaletching; and

(4) a step of forming a compressive-stress layer on the surfaces of theshape-processed glass substrate by subjecting the glass to chemicalstrengthening.

Step (1):

Step (1) is the step of melting glass materials in which the componentshave been formulated and blended so as to provide the glass substratewith the aforementioned glass composition.

More specifically, the glass materials corresponding to theaforementioned components are measured and blended, are placed in amelting pot made, for example, of fire brick, platinum, or a platinumalloy, where they are heated and molten, and then are subjected torefining and homogenization, thereby preparing molten glass having adesired composition.

Step (2):

Step (2) is the step of forming the molten glass having the desiredcomposition, which has been prepared in Step (1), into a plate-likeshape. In the present embodiment, it is preferable to use a down-drawprocess for this forming step. The down-draw process is a known processdisclosed, for example, in JP-A-2009-203080. In the down-draw process,molten glass is fed into a trough which is provided on a forming bodyand is made to flow over both sides of the trough. The overflowed moltenglass flows downward along both the side surfaces of the forming bodyhaving a wedge-shaped cross section and located below the trough,creating two flows of molten glass which join at the lowermost end ofthe forming body. The joining of the two flows results in a strip ofglass, which is drawn by drawing rollers provided below the formingbody. Thus, the molten glass is formed into a strip of glass having apredetermined thickness.

There are various processes for forming glass into a plate-like shape,including various down-draw processes, the float process, the re-drawprocess, and the roll-out process. Any one of these processes can beemployed, but in the present embodiment, it is most suitable to employthe down-draw process—and particularly the overflow down-draw process.The down-draw process is employed because glass substrates formed byusing the down-draw process are improved in etching rate, as compared toother forming processes such as the float process. Another reason isthat the principal surfaces of a glass substrate formed by using thedown-draw process are extremely smooth, because they are made by hotforming.

In contrast, with the known float process, a diffusion layer of tin (Sn)is formed on the glass surface, and this gives rise to a difference indiffusion rate of alkali ions between the front and back principalsurfaces of the glass at the time of chemical strengthening, thus posingdifficulty in forming the compressive-stress layer stably. Meanwhile,the press-forming process suffers in that large plate-shaped substratescannot be produced. With the other sheet-forming processes, the producedglass substrate cannot be employed as a cover glass unless the principalsurfaces are polished, leading to an increase in processing cost. Thedown-draw process employed in the present embodiment has none of thesedisadvantages.

A glass substrate formed into a sheet by the down-draw process can bemade extremely smooth and thin. Therefore, in the case ofshape-processing the glass substrate by etching, the glass substrate canbe etched evenly from both the principal surfaces thereof at the time ofetching the glass substrate from the principal surfaces thereof thathave resist patterns thereon serving as masks. In other words, theuniform composition of the glass substrate enhances the dimensionalaccuracy in etching and also improves the sectional shape of the endsurfaces of the cover glass, which may be used in a mobile phone, atouch-panel display, etc.

Also, both the principal surfaces of the glass substrate formed by usingthe down-draw process have a uniform composition, and therefore, therewill be no difference in the ion-exchange rate between the principalsurfaces during the later-described ion-exchange process. Thus, theglass substrate can be prevented from warping after ion exchange due toa difference in composition. In other words, it becomes possible toproduce homogeneous cover glasses, to improve productivity, and toreduce costs.

Further, forming the glass into a plate-like shape by using thedown-draw process can do away with the polishing step after forming,thus further reducing costs and improving productivity. Also, forming byusing the down-draw process can produce glass substrates with surfaceshaving no microcracks, which, in turn, can improve the strength of theglass substrates.

Step (3):

Step (3) is the shape-processing step by subjecting the plate-shapedglass substrate to at least chemical etching, to process the glasssubstrate into a desired shape. Note that “shape-processing” refers tothe forming of the shape of the principal surfaces of the formed glasssubstrate, and does not include the processing of only the end surfacesof the glass substrate.

The following explains how the cover glass is subjected to etching forthe shape-processing thereof prior to the ion-exchange processing step.

First, both the principal surfaces of the plate-shaped glass substrateprepared as above are coated with a resist material. Then, the resistmaterial is exposed via a photo mask having a desired outer-shapepattern. The outer shape is not particularly limited, and it may be anouter shape including, for example, sections having negative curvatures,as illustrated in FIG. 1.

Next, the exposed resist material is developed to thus form a resistpattern on the glass substrate in regions other than theregions-to-be-etched, and then, the regions-to-be-etched on the glasssubstrate are etched. If a wet etchant is used as the etchant, the glasssubstrate will be etched isotropically. Thus, each end surface of theglass substrate will be formed so as to have: a central section thatprojects outward the most; and sloped faces that curve gently from thecentral section toward the respective principal surfaces. It ispreferable that the boundaries between the sloped faces and therespective principal surfaces and the boundary between the two slopedfaces are rounded.

The resist material to be used in the etching step is not particularlylimited, and it is possible to use a material that is resistant to theetchant used for etching the glass while using the resist pattern as amask. For example, glass is, in general, corroded by wet etching usingan aqueous solution containing hydrofluoric acid or by dry etching usinga fluorine-based gas, so resist materials having excellent resistance tohydrofluoric acid are suitable. As for the etchant, it is possible tosuitably use hydrofluoric acid, or a mixed acid containing hydrofluoricacid and at least one of sulfuric acid, nitric acid, hydrochloric acid,and hydrofluorosilicic acid. The use of hydrofluoric acid or theaforementioned mixed-acid aqueous solution as the etchant can producecover glasses with desired shapes.

The etchant used for effectively dissolving the glass contains hydrogenfluoride. In the etching process, the fluorine (F) in the hydrogenfluoride (HF) bonds with the dissolved metal ions contained in the glasscomponents, and fluorine compounds precipitate in the etchant. Thefluorine compounds include calcium fluoride, magnesium fluoride, andaluminum fluoride. If these precipitates are produced, they will adhereto the glass surface during etching, thereby inhibiting the progress ofetching. Calcium fluoride, in particular, has a high production rate andextremely low solubility once it precipitates. So, in order to inhibitthe production of calcium fluoride during the etching step, it iseffective to reduce the amount of CaO introduced in the glasscomponents, or substantially not introduce CaO at all.

Further, even complicated outer shapes can be created easily, just byadjusting the mask pattern at the time of performing shape-processing byemploying etching. Further, performing shape-processing through etchingcan further improve productivity and also cut down processing costs. Asfor the stripping solution for stripping the resist material off fromthe glass substrate, an alkaline solution such as KOH or NaOH may beused. The type of resist material, etchant, and stripping solution canbe selected as appropriate depending on the material of the glasssubstrate.

Note that the etching method is not limited to the method of simplyimmersing the glass substrate into an etching solution, but instead itis possible to employ, for example, spray etching in which the etchingsolution is sprayed. The method of immersing the glass substrate into anetching solution is preferred over the spray-etching method because ofthe simplicity of the device and etching process. The immersion method,however, is prone to cause precipitations, such as calcium fluoride, toadhere to the glass surface during etching, and thus there is asignificant need to improve the etching rate. By employing the glasscomposition of the present embodiment, it is possible to preventprecipitations, such as calcium fluoride, from adhering to the glasssurface during etching. In other words, by employing the glasscomposition of the present embodiment, the cover glass can beshape-processed quickly, and with high accuracy, by a simpler method.

The glass substrate of the present embodiment has an etchingcharacteristic in which the etching rate is at least 3.7 μm/minute in anetching environment having a temperature of 22° C. and containinghydrogen fluoride with a concentration of 10% by mass. The above etchingcharacteristic can be achieved by adjusting the composition of the glasssubstrate in a manner such that, if the content of the aforementionedSiO₂ is X % and the content of the aforementioned Al₂O₃ is Y %, X−1/2·Yis 57.5% or less.

The above method gives an example of performing shape-processing on theglass substrate by using only chemical etching, but the presentembodiment is not limited thereto. For example, the shape-processing onthe glass substrate may be performed by using chemical etching andmachining in combination. For example, after shape-processing byetching, there may be a step of grinding or polishing some sections (theend surfaces, edges, etc.) of the glass substrate. Alternatively, priorto shape-processing by etching, there may be a step of cutting the glasssubstrate in advance by machining or a step of performing roughshape-processing.

The glass substrate of the present embodiment can also be suitably usedin cases where an etching step is provided with the aim of removingcracks from the end surfaces of the glass substrate. This is becausechemical substances, such as fluorine compounds, can precipitate in theetchant and deteriorate the etching accuracy and/or etching rate notonly in cases where the glass substrate is subjected toshape-processing, but also in an etching step having the aim of removingcracks from the end surfaces of the glass substrate. In other words, theglass substrate of the present embodiment can suitably be used in casesthat involve a processing step employing at least chemical etching. Forexample, the glass substrate of the present embodiment can suitably beused in such processing methods as described in (a) to (e) below thatinvolve a shape-processing step and a step of removing cracks in the endsurfaces of the glass substrate.

(a) A processing method involving: shape-processing by forming a resistfilm and sand-blasting thereon; then shape-processing the outerperipheral sections with diamond and other grindstones; and thenremoving remaining cracks on the processed surfaces by etching the glasssubstrate.

(b) A processing method involving: bonding a protective film on theprincipal surface of the glass; machining (e.g., cutting,shape-processing, boring) the glass; and then removing microcracks byetching the outer peripheral sections.

(c) A processing method involving: shape-processing by grinding andpolishing; and then removing remaining cracks by etching the entireglass substrate (including the principal surfaces and end surfacesthereof).

(d) A processing method involving: bonding two sheets of machined glasssubstrates together with a hot-melt wax or a UV-curable resin; and thenremoving remaining cracks by chemically etching the exposed outerperipheral sections.

(e) A processing method involving: laminating and bonding together aplurality of sheets of glass substrates with a hot-melt wax or aUV-curable resin; cutting the block consisting of the glass substratesand processing the outer periphery thereof; and then removing remainingcracks by chemically etching the processed surfaces (outer-peripheralend surfaces) that are exposed from the block.

Step (4):

Step (4) is the step of subjecting the glass substrate shape-processedin Step (3) to an ion-exchange process.

The cover glass according to the present embodiment is produced byperforming an ion-exchange process on the glass substrate that has beenshape-processed in Step (3) as described above. More specifically, forexample, after being rinsed, the glass substrate is immersed for around1 to 25 hours in a treatment bath containing 100% of KNO₃ and kept ataround 350° C. to 550° C., to thereby exchange the Na⁺ ions on thesuperficial layer of the glass with K⁺ ions present in the treatmentbath. In this way, the glass substrate can be chemically strengthened.Note that the temperature, the length of time, the ion-exchange salt,etc., for the ion-exchange process can be changed as appropriate. Forexample, the ion-exchange salt may be a mixture containing two or moretypes of compounds, such as a mixed salt of KNO₃ and NaNO₃.

Characteristics of Glass Substrate:

Next, the characteristics of the glass substrate to be used for thecover glass 10, 100 of the first and second embodiments will bedescribed.

Etching Rate:

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has an etching rate of 3.7 μm/minute or greater,preferably 4.3 μm/minute or greater, more preferably 4.5 μm/minute orgreater, and particularly preferably 5 μm/minute or greater, as measuredaccording to the method described below. By setting the etching ratewithin the aforementioned range, the rate for shape-processing the glassand the rate for processing the end surfaces by etching can beincreased, and the ability to produce the cover glass 10, 100 can beimproved. Although the ability to produce the cover glass 10, 100 isimproved with the increase in etching rate, increasing the content bypercentage of Al₂O₃ to increase the etching rate will also increase thedevitrification temperature. So, in order to achieve bothdevitrification resistance and an improvement in etching rate, it ispreferable that the glass constituting the glass substrate of thepresent embodiment has an etching rate of 10 μm/minute or less, morepreferably 8 μm/minute or less, and even more preferably 7 μm/minute orless. Specifically, the etching rate is preferably 3.7 μm/minute to 10μm/minute, more preferably 4.3 μm/minute to 10 μm/minute, even morepreferably 4.5 μm/minute to 8 μm/minute, and particularly preferably 5μm/minute to 7 μm/minute.

The etching rate is found by measuring the etching amount (the change inthickness) for when etching is conducted for 20 minutes in an etchingenvironment having a temperature of 22° C. and containing hydrogenfluoride with a concentration of 10% by mass.

Density:

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has a density of preferably 2.8 g/cm³ or less,more preferably 2.7 g/cm³ or less, even more preferably 2.6 g/cm³ orless, further more preferably 2.55 g/cm³ or less, and particularlypreferably 2.5 g/cm³ or less. The smaller the density of the glass, themore lightweight the glass can be made, and lightweight glass cansuitably be used as cover glasses, touch-panel display substrates, andthe like.

Linear Thermal Expansion Coefficient:

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has a linear thermal expansion coefficient ofpreferably from 50×10⁻⁷ to 120×10⁻⁷/° C., more preferably from 60×10⁻⁷to 120×10⁻⁷/° C., even more preferably from 70×10⁻⁷ to 110×10⁻⁷/° C.,and particularly preferably from 80×10⁻⁷ to 110×10′⁷/° C., within thetemperature range of 100° C. to 300° C. By setting the linear thermalexpansion coefficient of the glass within the range of 50×10⁻⁷ to120×10⁻⁷/° C. in the temperature range of 100° C. to 300° C., thecoefficient of thermal expansion will likely match the coefficients ofthermal expansion of peripheral materials, such as metals and organicadhesives, and thus the peripheral materials can be prevented frompeeling.

Devitrification Temperature (T1):

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has a devitrification temperature of preferably1200° C. or less, more preferably 1100° C. or less, even more preferably1000° C. or less, and particularly preferably 960° C. or less. The lowerthe devitrification temperature is, the more the devitrification ofglass during production can be prevented. In other words, lowerdevitrification temperatures can improve devitrification resistance, andthe glass becomes more suitable for down-draw processing and can beformed at lower temperatures, which thus allows the reduction of glassproduction costs. Also, lower devitrification temperatures can improvethe formability of glass. Note that “devitrification resistance” as usedherein is a characteristic that uses the devitrification temperature asits index: the lower the devitrification temperature, the higher thedevitrification resistance.

Glass Transition Temperature (Tg):

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has a glass transition temperature Tg of 500° C.or higher, preferably 510° C. or higher, more preferably 530° C. orhigher, even more preferably 560° C. or higher, further more preferably580° C. or higher, and particularly preferably 590° C. or higher. Bysetting Tg to 500° C. or higher, it is possible to prevent the heatresistance from deteriorating and the strengthening layer, which isformed on the principal surfaces and the end surfaces of the glasssubstrate by ion-exchange processing, from causing stress relaxation.Further, setting Tg to 500° C. or higher can inhibit the deformation ofthe glass substrate and the chemically-strengthened glass substrateduring thermal treatments, but if Tg reaches 700° C. or higher, theion-exchange performance will drop. Therefore, Tg is preferably 700° C.or lower, more preferably 650° C. or lower, and even more preferably620° C. or lower. Specifically, Tg is preferably 500° C. to 700° C.,preferably 510° C. to 700° C., more preferably 530° C. to 650° C., evenmore preferably 560° C. to 650° C., further more preferably 580° C. to650° C., and particularly preferably 590° C. to 620° C.

Further, the smaller the difference between the devitrificationtemperature and the glass transition point is, the more thedevitrification of glass during production can be prevented (the morethe devitrification resistance can be improved). That is, the smallerthe difference between the devitrification temperature and the glasstransition point is, the more the devitrification resistance can beimproved, and the glass becomes more suitable for down-draw processingand the glass substrate can be formed at lower temperatures, which thusallows the reduction of glass production costs. Therefore, in the glasssubstrate to be used for the cover glass 10, 100 of the presentembodiment, the difference “T1−Tg” is preferably 500° C. or less, morepreferably 450° C. or less, even more preferably 400° C. or less,further more preferably 380° C. or less, and particularly preferably370° C. or less. By setting the difference “T1−Tg” to 500° C. or less,the formability of the glass substrate can be improved.

High-Temperature Viscosity:

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has a high-temperature viscosity (temperature at200 dPa·s) of preferably 1700° C. or lower, more preferably 1600° C. orlower, even more preferably 1550° C. or lower, and particularlypreferably 1520° C. or lower. By setting the high-temperature viscosityof the glass substrate to 1700° C. or lower, it is possible to preventan increase in melting temperature as well as an increase in thermalload on the glass-production facility, such as the melting furnace. Thebubble quality (the content of bubbles) of the glass can also beimproved. Thus, glass can be produced inexpensively.

Strain Point:

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has a strain point of preferably 460° C. orhigher, more preferably 470° C. or higher, even more preferably 490° C.or higher, further more preferably 520° C. or higher, and particularlypreferably 560° C. or higher. By setting the strain point to 460° C. orhigher, it is possible to prevent the heat resistance from deterioratingand the strengthening layer, which is formed on the principal surfacesand the end surfaces of the glass substrate by ion-exchange processing,from causing stress relaxation. Note that, although setting the strainpoint to 460° C. or higher can inhibit the deformation of the glasssubstrate and the chemically-strengthened glass substrate during thermaltreatments, if the strain point reaches 660° C. or higher, theion-exchange performance will drop. Therefore, the strain point ispreferably 660° C. or lower, more preferably 610° C. or lower, and evenmore preferably 580° C. or lower. Specifically, the strain point ispreferably 460° C. to 660° C., more preferably 470° C. to 660° C., evenmore preferably 490° C. to 610° C., further more preferably 520° C. to610° C., and particularly preferably 560° C. to 580° C.

Thickness:

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has a thickness of preferably 3.0 mm or less,more preferably 2.0 mm or less, even more preferably 1.3 mm or less,further more preferably 0.8 mm or less, and particularly preferably 0.6mm or less. The thinner the glass substrate and thechemically-strengthened glass plate are, the more the cover glasses 10,100 can be made lightweight, which makes them suitable for coverglasses, touch-panel display substrates, and the like. Note that, inconsideration of the flexure, rigidity, strength, etc., of the glasssubstrate, the thickness is preferably 0.2 mm or greater, morepreferably 0.3 mm or greater, and even more preferably 0.4 mm orgreater. Meanwhile, chemically-strengthened glass that has beensubjected to ion-exchange processing is less prone to break even whenthe thickness is small. For example, by forming the glass substrate by adown-draw process, it is possible to produce a thin glass substrate withhigh mechanical strength and excellent surface accuracy, even withoutpolishing etc. Specifically, the thickness of the glass substrate andthe thickness of the chemically-strengthened glass plate are preferably0.2 mm to 2.0 mm, more preferably 0.2 mm to 1.3 mm, even more preferably0.4 mm to 1.3 mm, further more preferably 0.4 mm to 0.8 mm, andparticularly preferably 0.4 mm to 0.6 mm.

Compressive-Stress Value:

The glass substrate to be used for the cover glass 10, 100 of the firstand second embodiments has a compressive-stress layer having acompressive-stress value of preferably 140 MPa or greater, morepreferably 300 MPa or greater, and more preferably 400 MPa or greater,even more preferably 500 MPa or greater, and further more preferably 600MPa or greater. By setting the compressive-stress value to 300 MPa orgreater, the cover glasses 10, 100 can be provided with sufficientstrength to protect displays, for example. Note that, although anincrease in the compressive-stress value will improve the glassstrength, this will also increase the impact occurring when thestrengthened glass is damaged. Therefore, in order to prevent anyaccidents caused by the impact, it is preferable that thechemically-strengthened cover glass 10, 100 of the present embodimenthas a compressive-stress value of 950 MPa or less, more preferably 800MPa or less, more preferably 750 MPa or less, and even more preferably700 MPa or less. Specifically, the compressive-stress value of the glassconstituting the chemically-strengthened glass substrate and the coverglass of the present embodiment is preferably 300 MPa to 950 MPa, morepreferably 400 MPa to 900 MPa, even more preferably 400 MPa to 800 MPa,and even further preferably 500 MPa to 800 MPa.

Compressive Layer Depth:

The compressive layer depth of the glass constituting thechemically-strengthened glass substrate and the cover glass of thepresent embodiment is 15 μm to 90 μm, preferably 20 μm to 85 μm, morepreferably 25 μm to 80 μm, even more preferably 30 μm to 70 μm, and evenfurther preferably 30 μm to 50 μm.

Note that there has been a tendency to reduce the plate thickness of thecover glass in recent years in order to reduce the weight, and althoughthis is accompanied by a reduction in the compressive layer depth, thereis a demand for having a compressive stress value that is apredetermined value or greater. Specifically, it is preferable that theplate thickness of the cover glass is 0.2 mm to 1.3 mm, the compressivelayer depth is 20 μm to 85 μm, and the compressive stress value is 300MPa to 950 MPa; it is more preferable that the plate thickness of thecover glass is 0.4 mm to 1.3 mm, the compressive layer depth is 25 μm to80 μm, and the compressive stress value is 400 MPa to 900 MPa; it iseven more preferable that the plate thickness of the cover glass is 0.4mm to 0.8 mm, the compressive layer depth is 30 μm to 70 μm, and thecompressive stress value is 400 MPa to 800 MPa; and it is even morepreferable that the plate thickness of the cover glass is 0.4 mm to 0.6mm, the compressive layer depth is 30 μm to 50 μm, and the compressivestress value is 500 MPa to 800 MPa.

EXAMPLES

Now, the present invention will be described in further detail belowaccording to Examples thereof. The present invention, however, is not tobe limited to the following Examples.

Preparation of Glass According to First Embodiment

First, glass materials (batches) were prepared by using general glassmaterials, i.e., silica, alumina, sodium sulfate, lithium carbonate,sodium carbonate, potassium carbonate, basic magnesium carbonate,calcium carbonate, tin dioxide, and zirconium oxide, so as to providethe glass compositions as shown in Tables 1 and 2 (Samples 1 to 28) andTables 3 and 4 (Samples 29 to 33). Each prepared batch was heated in anelectric furnace for 4 hours at 1550° C. with a platinum crucible andwas made into molten glass, and then, outside the furnace, the moltenglass was spread out onto an iron plate to cool, to thereby prepare ablock of glass. The glass block was kept in an electric furnace for 30minutes at 600° C., then the furnace was turned off, and the glass blockwas gradually cooled to room temperature. The prepared glass block wasemployed as the glass sample for evaluating the physical properties ofthe glass.

For each glass sample prepared as above, the devitrificationtemperature, the strain point, the coefficient of thermal expansion, theglass transition temperature, the high-temperature viscosity, and theetching rate were evaluated.

Glass composition (mass %) Sample SiO₂ Al₂O₃ Li₂O Na₂O K₂O MgO CaO ZrO₂SnO₂ SO₃ 1 62.6 17.4 15.4 1.9 2.6 0.1 2 62.8 14.7 15.8 2.2 3.2 1.2 0.1 360.2 13.1 14.5 3.3 2.2 3.2 3.4 0.1 4 62.4 13.1 14.5 3.3 2.2 3.2 1.2 0.15 60.8 14.7 14.5 3.3 2.2 3.2 1.2 0.1 6 61.3 12.8 12.9 3.3 2.2 3.2 4.20.1 7 56.0 17.3 14.5 3.3 2.2 3.2 3.4 0.1 8 58.0 15.3 14.5 3.3 2.2 3.23.4 0.1 9 62.0 11.3 14.5 3.3 2.2 3.2 3.4 0.1 10 60.2 13.1 14.5 3.3 3.91.5 3.4 0.1 11 54.0 19.3 14.5 3.3 2.2 3.2 3.4 0.1 12 62.1 12.8 15.5 3.26.3 0.1 13 60.9 12.1 17.7 3.1 4.1 2.0 0.1 14 59.7 11.8 17.4 3.1 4.0 3.80.1 15 61.0 10.9 17.7 6.3 2.1 2.0 0.1 16 59.8 10.7 17.4 6.2 2.0 3.8 0.117 59.9 10.5 12.4 9.2 4.0 3.8 0.1 18 62.0 13.0 20.7 4.2 0.1 19 62.0 13.319.4 5.3 0.1 20 62.1 12.9 18.1 1.6 5.3 0.1 21 60.9 13.0 12.8 7.9 5.2 0.122 60.9 12.0 15.2 4.7 5.1 2.0 0.1 23 61.5 14.0 15.3 3.8 5.2 0.1 24 60.813.7 15.4 4.8 5.2 0.1 25 60.1 14.5 15.3 4.8 5.2 0.1 26 62.0 14.1 14.93.8 5.2 0.1 27 62.2 14.1 15.3 3.1 5.2 0.1 28 61.9 14.0 15.3 3.8 4.9

TABLE 2 Glass composition (%) SiO₂-1/ B₂O₃/ (ZrO₂ + TiO₂)/ Li₂O/ SampleRO 2Al₂O₃ R¹ ₂O SiO₂ (RO +Li₂O) 1 4.5 53.9 0 0 0 2 5.4 55.5 0 0.019 0 35.4 53.7 0 0.056 0 4 5.4 55.9 0 0.019 0 5 5.4 53.5 0 0.020 0 6 5.4 53.70 0.080 0 7 5.4 47.4 0 0.061 0 8 5.4 50.4 0 0.059 0 9 5.4 56.4 0 0.055 010 5.4 53.7 0 0.056 0 11 5.4 44.4 0 0.063 0 12 6.3 55.7 0 0 0 13 4.154.9 0 0.032 0 14 4.0 53.8 0 0.064 0 15 2.1 55.5 0 0.032 0 16 2.0 54.5 00.064 0 17 4.0 54.7 0 0.064 0 18 4.2 55.5 0 0 0 19 5.3 55.4 0 0 0 20 5.355.6 0 0 0 21 5.2 54.4 0 0 0 22 5.1 55.0 0 0.032 0 23 5.2 54.5 0 0 0 245.2 53.9 0 0 0 25 5.2 52.9 0 0 0 26 5.2 55.0 0 0 0 27 5.2 55.1 0 0 0 284.9 54.9 0 0 0

TABLE 3 Glass composition (mass %) Sample SiO₂ Al₂O₃ Li₂O Na₂O K₂O MgOCaO ZrO₂ SnO₂ SO₃ 29 65 8.3 14.5 3.3 2.2 3.2 3.4 0.1 30 67 6.3 14.5 3.32.2 3.2 3.4 0.1 31 63.2 10.1 14.5 3.3 2.2 3.2 3.4 0.1 32 63.7 9.7 14.53.3 2.2 3.2 3.4 0.1 33 63.5 8.0 7.8 10.2 11.2

TABLE 4 Glass composition (%) SiO₂-1/ B₂O₃/ (ZrO₂ + TiO₂)/ Li₂O/ SampleRO 2Al₂O₃ R¹ ₂O SiO₂ (RO + Li₂O) 29 5.4 60.9 0 0.052 0 30 5.4 63.9 00.051 0 31 5.4 58.1 0 0.054 0 32 5.4 58.9 0 0.053 0 33 0 59.5 0 0.176 1

Evaluation of Devitrification Temperature:

The glass sample was pulverized, and glass particles that passed througha 2380-μm sieve but remained on a 1000-μm sieve were immersed intoethanol, subjected to ultrasonic cleaning, and then dried in aconstant-temperature oven. Then, 25 g of the glass particles were placedon a 12-by-200-by-10-mm platinum board so that they assume asubstantially constant thickness, and were placed in an electric furnacehaving a temperature gradient from 800° C. to 1200° C. and kept thereinfor 24 hours. Then, the particles were taken out from the furnace, anddevitrification that occurred inside the glass was observed with anoptical microscope at a magnification of 40 times. The maximumtemperature at which devitrification was observed was found as thedevitrification temperature.

Evaluation of Strain Point:

The glass sample was cut out into a 3-by-3-by-55-mm right square prismand was ground, and the strain point (Ps) thereof was measured with abeam bending viscometer (product of Tokyo Kogyo Co., Ltd.). The strainpoint was found by calculation according to the beam bending method(ASTM C-598).

Evaluation of Coefficient of Thermal Expansion and Glass TransitionTemperature (Tg):

The glass sample was processed into a circular cylinder 5 mm in diameterand 20 mm long, and the coefficient of thermal expansion and the glasstransition temperature (Tg) were measured with a differentialdilatometer (Thermo Plus2 TMA8310). The average thermal expansioncoefficient in the temperature range of 100° C. to 300° C. wascalculated from the results of measuring the thermal expansioncoefficient.

Evaluation of Density:

The density was measured according to the Archimedean method.

Evaluation of High-Temperature Viscosity:

The glass sample was molten for 4 hours at 1600° C. and bubbles wereremoved therefrom, and the high-temperature viscosity was measured witha pull-down automatic viscometer. More specifically, the viscosity ofthe sample was found by suspending a platinum ball down into the moltenglass sample, pulling down the sample and the container containing thesame, and measuring the viscous drag applied on the ball as the sampleand the container were pulled down, as the load. Tables 5 and 6 show thetemperature for when the glass viscosity was 200 dPa·s.

Evaluation of Etching Rate:

The glass sample was cut into a size 20 to 50 mm long, 20 to 40 mm wide,and 0.7 mm thick and was ground and polished, to prepare a sample sheet.After being rinsed, the sample sheet was immersed for 20 minutes in 400mL of HF (concentration: 10% by mass; temperature: 22° C.) held in acontainer. After rinsing the sample sheet with water, the thickness andmass of the sample were measured and compared with those measured priorto the test, to calculate the etching rate of the glass sample.

Chemical Strengthening:

The sample sheet, after being rinsed, was immersed for about 2.5 hoursin a treatment bath containing 100% of KNO₃ kept at 400° C., to exchangethe Na⁺ ions on the superficial layer of the glass with K⁺ ions presentin the treatment bath and thereby chemically strengthen the glasssample. The chemically-strengthened glass substrate was immersed in arinsing tank for rinsing and then dried, to thereby obtain a piece ofstrengthened glass. As for Samples 4, 7, 9, and 10, each glass samplewas chemically strengthened by being immersed for about 5 hours in atreatment bath containing 100% of KNO₃ kept at 500° C.

Evaluation of Compressive-Stress Value:

The strengthened glass obtained as above was observed to find the numberof interference fringes and the interval therebetween with a surfacestress meter (Luceo FSM-6000LE), and the compressive-stress value of thecompressive-stress layer formed in the vicinity of the surface of theglass and the thickness of the compressive-stress layer were calculated.In the calculation, the refractive index (nd) of each sample wasregarded as 1.50, and the stress optical coefficient was regarded as 28((nm/cm)/MPa). As for samples 4, 7, 9, and 10, the refractive index (nd)of each sample was regarded as 1.52.

Tables 5 and 6 show the characteristics of Samples 1 to 28 of the firstembodiment shown in Tables 1 and 2 and those of Samples 29 to 33 of thefirst embodiment shown in Tables 3 and 4.

Glass characteristics High- Compres- Surface temp Avg. thermal sivecompres- viscos- Strain expan- stress sive layer Tl ity point Etchingrate Tg sion coef. Tl-Tg Density value depth Sample (° C.) (° C.) (° C.)(μm/min) (° C.) [×10⁻⁷/° C.] (° C.) (μ/cm³) (MPa) (μm)  1 1000 563 5.1610 89 390 2.46  2 1021 558 4.5 604 89 417 2.49  3 948 1508 563 5.2 59395 355 2.52 659 40  4 927 532 4.3 578 97 349 2.49  5 988 545 5.3 592 97396 2.49  6 1003 1542 582 5.2 616 90 387 2.54 768 35  7 1018 583 6.1 62691 392 2.53  8 1003 570 6.1 614 91 389 2.53 864 41  9 968 537 4.1 586 91382 2.51 707 36 10 1112 579 5.2 620 91 492 2.50 11 1200 587 4.8 636 92564 12 1090 3.7 585 99.7 505 2.455 693 47 13 <840 4.0 559 106 <300 2.480543 57 14 <840 4.6 579 97.9 <300 2.510 684 53 15 <840 3.7 511 114 <3292.477 147 88 16 <840 4.2 527 113 <313 2.506 236 83 17 <840 4.1 572 106<300 2.502 587 66.8 18 <840 3.7 551 102.7 <300 2.460 354 53.4 19 <8403.8 574 99.5 <300 2.457 524 47.7 20 <840 3.7 566 102.7 <300 2.453 57649.4 21 <840 4.2 570 105 <300 2.449 584 65 22 <840 3.9 581 102.6 <3002.487 23 907 4.2 574 104 333 2.459 24 <840 4.5 572 103.6 <300 2.463 25953 5.2 577 105 376 2.465 26 <840 3.9 <300 27 <840 3.9 <300 28 <840 4.0<300

TABLE 6 Glass characteristics High-temp. Strain Etching Avg. thermal Tlviscosity point rate Tg expansion Tl-Tg Density Sample (° C.) (° C.) (°C.) (μm/min) (° C.) [×10⁻⁷/° C. ] (° C.) (g/cm³) 29 858 513 2.3 563 90295 2.51 30 830 504 1.7 554 90 276 2.50 31 855 530 3.4 576 90 279 2.5132 836 527 2.8 571 90 265 2.51 33 524 3.5 570

FIG. 3 shows a distribution chart showing the etching rates given onTables 5 and 6 on the Y-axis and the aforementioned X−1/2·Y (wherein Xis the content by percentage of SiO₂ and Y is the content by percentageof Al₂O₃) on the X-axis for Samples 1 to 28 in Tables 1 and 2 andSamples 29 to 33 in Tables 3 and 4. As can be seen, the etching rateincreases as the value of X−1/2·Y decreases. Meanwhile, no significantchange in the etching rate can be seen in the area where X−1/2·Y is 52%or less. So, in order to achieve an etching rate of 3.7 μm/minute orgreater, it is preferable that X−1/2·Y is 57.5% or less. However, evenif the value of Y is increased and X−1/2·Y is adjusted to 52% or less,there will be no further increase in the etching rate, and in addition,the devitrification temperature will increase and thus thedevitrification resistance will deteriorate. Therefore, the lower limitof the value of X−1/2·Y is preferably 45%.

Example of Continuous Production of Glass Substrate:

Glass materials were prepared so as to provide a glass substrate withthe composition shown in Sample 4 (see Tables 1 and 2). The glassmaterials were molten at 1520° C. by using a continuous melting devicehaving, for example, a fire-brick-made melting tank, a platinum-madestirring tank and so on, were subjected to refining at 1550° C., stirredat 1350° C., and then formed into a thin plate 0.7 mm thick by down-drawprocessing, to produce a glass substrate for chemical strengthening.Etching and chemical strengthening were performed as follows.

The glass substrate prepared as above was employed as the sample glasssubstrate, and a 20-μm-thick pattern made of a phenolic heat-curableresin and having the shape of a cover glass was formed on each of theprincipal surfaces of the substrate by mesh-screen printing, and thephenolic heat-curable resin patterns were baked for 15 minutes at 200°C. With the phenolic heat-curable resin patterns being employed asmasks, the glass sample was etched in the regions-to-be-etched from bothprincipal surfaces by using a mixed-acid aqueous solution (40° C.)containing hydrofluoric acid (15% by mass) and sulfuric acid (24% bymass) as the etchant, to cut the glass sample into a predeterminedshape. Then, the phenolic heat-curable resin remaining on the glass wasdissolved by using an NaOH solution and was removed off from the glass,and then the glass was rinsed.

Then, the rinsed sample glass substrate was immersed for about 5 hoursin a treatment bath containing 100% of KNO₃ kept at 500° C., to exchangethe Na ions on the superficial layer of the glass with K ions present inthe treatment bath and thereby chemically strengthen the glass sample.The chemically-strengthened sample glass substrate was immersed in arinsing tank for rinsing and then dried. The result was that it waspossible to produce a glass substrate having excellent quality and animproved etching rate of 3.7 μm/minute or higher.

Preparation of Glass according to Second Embodiment

First, glass materials (batches) were prepared by using general glassmaterials, i.e., silica, alumina, sodium sulfate, lithium carbonate,sodium carbonate, potassium carbonate, basic magnesium carbonate,calcium carbonate, tin dioxide, and zirconium oxide, so as to providethe glass compositions as shown in Tables 7 and 8 (Samples 34 to 62) andTables 9 and 10 (Samples 63 to 76). Each prepared batch was heated in anelectric furnace for 4 hours at 1550° C. with a platinum crucible andwas made into molten glass, and then, outside the furnace, the moltenglass was spread out onto an iron plate to cool, to thereby prepare ablock of glass. The glass block was kept in an electric furnace for 30minutes at 600° C., then the furnace was turned off, and the glass blockwas gradually cooled to room temperature. The cooled glass block wassubjected to machining, such as cutting and polishing, and was made intoa 50-by-40-mm glass sample approximately 0.7 mm thick. For each glasssubstrate prepared as above, the devitrification temperature (Tl), theetching rate, the glass transition temperature (Tg), the average linearthermal expansion coefficient, the density, the compressive-stressvalue, the surface compressive layer depth, and the processing accuracywere evaluated.

TABLE 7 Glass composition (mass %) Sample SiO₂ Al₂O₃ Li₂O Na₂O K₂O MgOCaO ZrO₂ SnO₂ SO₃ 34 62.6 17.4 15.4 1.9 2.6 0.1 35 60.2 13.1 14.5 3.33.9 1.5 3.4 0.1 36 62.1 12.8 15.5 3.2 6.3 0.1 37 60.9 12.1 17.7 3.1 4.12.0 0.1 38 59.7 11.8 17.4 3.1 4.0 3.8 0.1 39 61.0 10.9 17.7 6.3 2.1 2.00.1 40 59.8 10.7 17.4 6.2 2.0 3.8 0.1 41 59.9 10.5 12.4 9.2 4.0 3.8 0.142 62.0 13.0 20.7 4.2 0.1 43 62.0 13.3 19.4 5.3 0.1 44 62.1 12.9 18.11.6 5.3 0.1 45 60.9 13.0 12.8 7.9 5.2 0.1 46 60.9 12.0 15.2 4.7 5.1 2.00.1 47 61.5 14.0 15.3 3.8 5.2 0.1 48 60.8 13.7 15.4 4.8 5.2 0.1 49 60.114.5 15.3 4.8 5.2 0.1 50 62.0 14.1 14.9 3.8 5.2 0.1 51 62.2 14.1 15.33.1 5.2 0.1 52 61.9 14.0 15.3 3.8 4.9 53 62.1 12.7 19.4 1.6 4.2 0.1 5462.2 12.2 15.5 4.8 5.3 0.1 55 62.2 12.4 14.7 4.8 5.9 0.1 56 62.1 12.716.0 3.2 5.9 0.1 57 61.5 14.3 15.3 3.2 5.6 0.1 58 61.5 14.0 0.001 15.43.8 5.2 0.1 59 61.5 14.0 0.01 15.4 3.8 5.2 0.1 60 61.5 14.0 0.04 15.43.8 5.2 0.1 61 61.5 14.0 0.10 15.4 3.8 5.2 0.1 62 61.3 14.0 0.4 15.4 3.85.2 0.1

TABLE 8 Glass composition SiO₂-1/ B₂O₃/ (ZrO₂ + Li₂O/ Sample RO 2Al₂O₃R¹ ₂O TiO₂)/SiO₂ (RO + Li₂O) 34 4.5 53.9 0 0.000 0 35 5.4 53.7 0 0.056 036 6.3 55.7 0 0 0 37 4.1 54.9 0 0.032 0 38 4.0 53.8 0 0.064 0 39 2.155.5 0 0.032 0 40 2.0 54.5 0 0.064 0 41 4.0 54.7 0 0.064 0 42 4.2 55.5 00 0 43 5.3 55.4 0 0 0 44 5.3 55.6 0 0 0 45 5.2 54.4 0 0 0 46 5.1 55.0 00.032 0 47 5.2 54.5 0 0 0 48 5.2 53.9 0 0 0 49 5.2 52.9 0 0 0 50 5.255.0 0 0 0 51 5.2 55.1 0 0 0 52 4.9 54.9 0 0 0 53 4.2 55.7 0 0 0 54 5.356.1 0 0 0 55 5.9 56.0 0 0 0 56 5.9 55.8 0 0 0 57 5.6 54.3 0 0 0 58 5.254.5 0 0 0.0002 59 5.2 54.5 0 0 0.0019 60 5.2 54.5 0 0 0.0076 61 5.254.4 0 0 0.0189 62 5.2 54.3 0 0 0.0714

TABLE 9 Glass composition (mass %) Sample SiO₂ Al₂O₃ Li₂O Na₂O K₂O MgOCaO ZrO₂ SnO₂ SO₃ 63 65.0 8.3 14.5 3.3 2.2 3.2 3.4 0.1 64 67.0 6.3 14.53.3 2.2 3.2 3.4 0.1 65 63.2 10.1 14.5 3.3 2.2 3.2 3.4 0.1 66 63.7 9.714.5 3.3 2.2 3.2 3.4 0.1 67 63.5 8.2 8.0 10.4 11.9 68 62.8 14.7 15.8 2.23.2 1.2 0.1 69 60.2 13.1 14.5 3.3 2.2 3.2 3.4 0.1 70 62.4 13.1 14.5 3.32.2 3.2 1.2 0.1 71 60.8 14.7 14.5 3.3 2.2 3.2 1.2 0.1 72 61.3 12.8 12.93.3 2.2 3.2 4.2 0.1 73 56.0 17.3 14.5 3.3 2.2 3.2 3.4 0.1 74 58.0 15.314.5 3.3 2.2 3.2 3.4 0.1 75 62.0 11.3 14.5 3.3 2.2 3.2 3.4 0.1 76 54.019.3 14.5 3.3 2.2 3.2 3.4 0.1

Glass composition Sample RO SiO₂-1/2Al₂O₃ B₂O₃/R¹ ₂O (ZrO₂ + TiO₂)/SiO₂Li₂O/(RO + Li₂O) 63 5.4 60.9 0 0.052 0 64 5.4 63.9 0 0.051 0 65 5.4 58.20 0.054 0 66 5.4 58.9 0 0.053 0 67 0 59.4 0 0.176 1 68 5.4 55.5 0 0.0190 69 5.4 53.7 0 0.056 0 70 5.4 55.9 0 0.019 0 71 5.4 53.5 0 0.020 0 725.4 54.9 0 0.069 0 73 5.4 47.4 0 0.061 0 74 5.4 50.4 0 0.059 0 75 5.456.4 0 0.055 0 76 5.4 44.4 0 0.063 0

Evaluation of Devitrification Temperature:

The glass sample was pulverized, and glass particles that passed througha 2380-μm sieve but remained on a 1000-μm sieve were immersed intoethanol, subjected to ultrasonic cleaning, and then dried in aconstant-temperature oven. Then, 25 g of the glass particles were placedon a 12-by-200-by-10-mm platinum board so that they assume asubstantially constant thickness, and were placed in an electric furnacehaving a temperature gradient from 800° C. to 1200° C. and kept thereinfor 24 hours. Then, the particles were taken out from the furnace, anddevitrification that occurred inside the glass was observed with anoptical microscope at a magnification of 40 times. The maximumtemperature at which devitrification was observed was found as thedevitrification temperature.

Evaluation of Etching Rate:

The glass sample, after being rinsed, was immersed for 20 minutes in 400mL of HF (concentration: 10% by mass; temperature: 22° C.) held in acontainer. After rinsing the sample with water, the thickness and massof the sample were measured and compared with those measured prior tothe test, to calculate the etching rate of the glass substrate.

Evaluation of Accuracy in Shape-Processing including Etching:

As illustrated in FIG. 4A, two sheets of glass 20, each of which being amachined glass substrate prior to chemical strengthening, were placed ontop of one another, and three sheets of dummy glass 22 were placed onthe respective sides of the two glasses 20, and the stack of glasssheets was etched. The etched end surfaces of the glass after etchingwere observed with an optical microscope.

The end surfaces were observed in two ways. Observation A was done byvisually observing the end surface on the long side of the glass, asillustrated in FIG. 4A, at 200× magnification. Observation B was doneby: first splitting the glass substrate in half at the center of theshort side thereof along a line perpendicular to the short side; andthen visually observing the end surface on the short side of the glass,as illustrated in FIG. 4B, at 200× magnification. The etching result wasevaluated as “Good” if both Observations A and B showed that etching wasachieved substantially evenly, was evaluated as “Fair” if only one ofObservations A and B showed that etching was achieved substantiallyevenly and the other was uneven, and was evaluated as “Poor” if bothObservations A and B showed that etching was uneven. For example, suchsample images as those shown in FIG. 5A are evaluated as “Poor”, whilesuch sample images as those shown in FIG. 5B are evaluated as “Good”. Asfor the sample images shown in FIG. 5A, the end surface of the glass hasprojections and recesses created by precipitations having precipitatedon the end surface, and is thus not smooth. Thus, the sample images inFIG. 5A for Observation A, which were obtained with an opticalmicroscope, show an intermixture of white regions created by specularreflection of light from the smooth areas of the glass end surface andblack regions created by diffused reflection of light from theprojections and recesses due to precipitations. Further, the sampleimage in FIG. 5A for Observation B shows a concave cross-sectionalshape. In contrast, the sample images in FIG. 5B for Observations A showclear boundaries between the white regions and the black regions. Thus,it is considered that the samples shown in FIG. 5B achieve high etchingaccuracy.

Evaluation of Coefficient of Thermal Expansion and Glass TransitionTemperature Tg:

The glass sample was processed into a circular cylinder 5 mm in diameterand 20 mm long, and the coefficient of thermal expansion and the glasstransition temperature Tg were measured with a differential dilatometer(Thermo Plus2 TMA8310). The average thermal expansion coefficient in thetemperature range of 100° C. to 300° C. was calculated from the resultsof measuring the thermal expansion coefficient.

Density:

The density was measured according to the Archimedean method.

Chemical Strengthening:

The glass sample, after being rinsed, was immersed for about 2.5 hoursin a treatment bath containing 100% of KNO₃ kept at 400° C., to exchangethe Na⁺ ions on the superficial layer of the glass with K⁺ ions presentin the treatment bath and thereby chemically strengthen the glasssample. The chemically-strengthened glass substrate was immersed in arinsing tank for rinsing and then dried, to thereby obtain a piece ofstrengthened glass. As for Samples 37, 40, 42, and 52, each glass samplewas chemically strengthened by being immersed for about 5 hours in atreatment bath containing 100% of KNO₃ kept at 500° C.

Evaluation of Compressive-Stress Value and Thickness (Depth) ofCompressive-Stress Layer:

The strengthened glass obtained as above was observed to find the numberof interference fringes and the interval therebetween with a surfacestress meter (FSM-6000LE from Orihara Industrial Co., Ltd.), and thecompressive-stress value of the compressive-stress layer formed in thevicinity of the surface of the glass and the thickness (depth) of thecompressive-stress layer were calculated. The value of the refractiveindex (nd) of each strengthened glass used for the calculation wasmeasured with a refractometer (KPR-200 from Shimadzu DeviceCorporation). Note that the stress optical coefficient was regarded as28 ((nm/cm)/MPa) in the calculation for the compressive-stress value.

Tables 11 and 12 show the evaluation results and other characteristicsof Samples 34 to 62 of the second embodiment shown in Tables 7 and 8 andthose of Samples 53 to 76 of the second embodiment shown in Tables 9 and10.

TABLE 11 Glass Characteristics Avg. thermal Surface Proc- Sam- TlEtching rate Tg expansion coef. Density Compressive- compressive essingple (° C.) (μm/min) (° C.) [×10⁻⁷/° C.] (g/cm³) stress value layer depthaccuracy 34 1000 5.1 610 89 2.46 Fair 35 1112 5.2 620 91 2.50 Fair 361090 3.7 585 99.7 2.455 693 47 Good 37 <840 4.0 559 106 2.480 543 57Good 38 <840 4.6 579 97.9 2.510 684 53 Good 39 <840 3.7 511 114 2.477147 88 Good 40 <840 4.2 527 113 2.506 236 83 Good 41 <840 4.1 572 1062.502 587 66.8 Good 42 <840 3.7 551 102.7 2.460 354 53.4 Good 43 <8403.8 574 99.5 2.457 524 47.7 Good 44 <840 3.7 566 102.7 2.453 576 49.4Good 45 <840 4.2 570 105 2.449 584 65 Good 46 <840 3.9 581 102.6 2.487Good 47 907 4.2 574 104 2.459 Good 48 <840 4.5 572 103.6 2.463 Good 49953 5.2 577 105 2.465 Good 50 <840 3.9 Good 51 <840 3.9 Good 52 <840 4.0Good 53 <950 3.7 544 107 2.46 350 56 Good 54 <950 3.7 558 102 2.46 52963 Good 55 <950 3.8 574 102 2.46 616 53 Good 56 <900 3.8 580 98 2.46 59154 Good 57 <900 3.7 586 101 2.46 705 50 Good 58 921 3.8 583 102 2.46 71951 Good 59 <850 3.8 578 102 2.45 660 54 Good 60 879 3.8 576 100 2.45 65554 Good 61 914 3.8 568 100 2.46 610 53 Good 62 <850 3.8 551 94 2.46 55952 Good

TABLE 12 Glass characteristics Avg. thermal Proc- Tl Etching rate Tgexpansion coef. Density essing Sample (° C.) (μm/min) (° C.) [×10⁻⁷/°C.] (g/cm³) accuracy 63 858 2.3 563 90 2.51 Poor 64 830 1.7 554 90 2.50Poor 65 855 3.4 576 90 2.51 Poor 66 836 2.8 571 90 2.51 Poor 67 3.5 570Poor 68 1021 4.5 604 89 2.49 Poor 69 948 5.2 593 95 2.52 Poor 70 927 4.3578 97 2.49 Poor 71 988 5.3 592 97 2.49 Poor 72 1003 5.2 616 90 2.54Poor 73 1018 6.1 626 91 2.53 Poor 74 1003 6.1 614 91 2.53 Poor 75 9684.1 586 91 2.51 Poor 76 1200 4.8 636 92 Poor

A comparison between Tables 11 and 12 reveals that Samples 34 and 35containing 2.6% or less of CaO and Samples 36 to 62 substantiallycontaining no CaO have high processing accuracies in the etching ofglass substrates. Note that the “processing accuracy” in Tables 11 and12 shows evaluation results for when etching is performed on the endsurfaces of glass substrates that have been machined, but even whenetching is performed with the aim of shape-processing a glass substrateto provide it with the shape as illustrated in FIG. 1, the evaluationresult on the processing accuracy thereof has the same tendency as theevaluation result for when etching is performed on the end surfaces of aglass substrate that has been machined. In other words, Samples 34 and35 containing 2.6% or less of CaO and Samples 36 to 62 substantiallycontaining no CaO can be considered as having high processing accuracieseven when etching is performed with the aim of shape-processing.

FIG. 6 shows a distribution chart showing the etching rates given onTables 11 and 12 on the Y-axis and the aforementioned X−1/2·Y (wherein Xis the content by percentage of SiO₂ and Y is the content by percentageof Al₂O₃) on the X-axis for Samples 34 to 62 in Tables 7 and 8 andSamples 63 to 76 in Tables 9 and 10. As can be seen, the etching rateincreases as the value of X−1/2·Y decreases. Meanwhile, no significantchange in the etching rate can be seen in the area where X−1/2·Y is 52%or less. So, in order to achieve an etching rate of 3.7 μm/minute orgreater, it is preferable that X−1/2·Y is 57.5% or less. However, evenif the value of Y is increased and X−1/2·Y is adjusted to 52% or less,there will be no further increase in the etching rate, and in addition,the devitrification temperature will increase and thus thedevitrification resistance will deteriorate. Therefore, the lower limitof the value of X−1/2·Y is preferably 45%.

Example of Continuous Production of Glass Substrate:

Glass materials were prepared so as to provide a glass substrate withthe composition shown in Sample 36 (see Tables 7 and 8). The glassmaterials were molten at 1520° C. by using a continuous melting devicehaving, for example, a fire-brick-made melting tank, a platinum-madestirring tank and so on, were subjected to refining at 1550° C., stirredat 1350° C., and then formed into a thin plate 0.7 mm thick by down-drawprocessing, to produce a glass substrate. Etching and chemicalstrengthening were performed as follows.

On each of the two principal surfaces of the glass substrate prepared asabove, a 20-μm-thick pattern made of a phenolic heat-curable resin andhaving the shape of a cover glass was formed by mesh-screen printing,and the phenolic heat-curable resin patterns were baked for 15 minutesat 200° C. With the phenolic heat-curable resin patterns being employedas masks, the glass substrate was etched in the regions-to-be-etchedfrom both principal surfaces by using a mixed-acid aqueous solution (40°C.) containing hydrofluoric acid (15% by mass) and sulfuric acid (24% bymass) as the etchant, to cut the glass substrate into a predeterminedshape. Then, the phenolic heat-curable resin remaining on the glasssurface was dissolved by using an NaOH solution and was removed off fromthe glass substrate, and then the substrate was rinsed.

Then, the rinsed glass substrate was immersed for about 5 hours in atreatment bath containing 100% of KNO₃ kept at 500° C., to exchange theNa ions on the superficial layer of the glass with K ions present in thetreatment bath and thereby chemically strengthen the glass substrate.The chemically-strengthened glass substrate was immersed in a rinsingtank for rinsing and then dried.

The result was that it was possible to produce a cover glass havingexcellent accuracy in shape.

As described above, with the cover-glass production method and the coverglass of the first embodiment, the etching rate can be improved, andthus the cover-glass production efficiency can be improved. Further,with the cover-glass production method and the cover glass of the secondembodiment, the cover glass can be produced with high accuracy in shape,even if the shape is complicated, and thus the cover-glass productionefficiency can be improved.

Certain embodiments of the cover glass and the cover-glass productionmethod of the present invention were described in detail above, but thepresent invention is not to be limited to the foregoing embodiments andcan be modified and/or improved in various ways as far as suchmodifications/improvements do not depart from the gist of the presentinvention.

What is claimed is:
 1. A method for producing a cover glass, comprising:subjecting a glass substrate to shape-processing by etching, the glasssubstrate having been formed into a plate-like shape by a down-drawingprocess and containing, as components thereof, 50% to 70% by mass ofSiO₂, 5% to 20% by mass of Al₂O₃, 6% to 30% by mass of Na₂O, and 0% toless than 8% by mass of Li₂O; and forming a compressive-stress layer onthe shape-processed glass substrate by subjecting the glass substrate tochemical strengthening.
 2. The method for producing a cover glassaccording to claim 1, wherein the glass substrate further contains, as acomponent thereof, 0% to 2.6% by mass of CaO.
 3. The method forproducing a cover glass according to claim 1, wherein, if the content bypercentage of the SiO₂ is X % by mass and the content by percentage ofthe Al₂O₃ is Y % by mass, X−1/2·Y is at most 57.5% by mass.
 4. Themethod for producing a cover glass according to claim 3, wherein theX−1/2·Y is at least 45% by mass.
 5. The method for producing a coverglass according to claim 1, wherein the etching is chemical etching. 6.A method for producing a cover glass, comprising: subjecting a glasssubstrate to shape-processing, the glass substrate having been formedinto a plate-like shape and containing, as components thereof, 50% to70% by mass of SiO₂, 5% to 20% by mass of Al₂O₃, 6% to 30% by mass ofNa₂O, 0% to less than 8% by mass of Li₂O, and 0% to 2.6% by mass of CaO;processing at least an end surface of the shape-processed glasssubstrate by chemical etching; and forming a compressive-stress layer onthe processed glass substrate by subjecting the glass substrate tochemical strengthening.
 7. The method for producing a cover glassaccording to claim 6, wherein, if the content by percentage of the SiO₂is X % by mass and the content by percentage of the Al₂O₃ is Y % bymass, X−1/2·Y is at most 57.5% by mass.